DE2307929A1 - METHOD OF MANUFACTURING IRON COBALT ALLOY MATERIAL - Google Patents

Description

DiPL-ING. KLAUS NEUBECKER

Patent attorney * s q Γ) "7 Q J ft

4 Düsseldorf 1 ■ Schadowplatz 9

Düsseldorf, February 16, 1973

40.208 \

Westinghouse Electric Corporation
Pittsburgh, Pa., V. St. A.

Process for the production of
Iron cobalt alloy material

The present invention relates to iron-cobalt alloys with improved magnetic properties and a method for making such alloys. Draw these alloys is characterized by a high grain volume with (110) [ooi] -laid texture that resulted from primary recrystallization and normal grain growth.

The working inductions of large areas of transformers as they are used today are due to the saturation value of aligned silicon steel, d. H. a steel with about 3% silicon and a high degree of (110) JjDOlj orientation. This saturation value is generally assumed to be 20,300 Gauss. Both from the economic and from the technological point of view From a standpoint, this is the highest quality transformer material currently commercially available.

In iron, cobalt has the effect that the saturation value of iron is considerably increased, with saturation inductions in the An order of magnitude of 24,000 Gauss can be observed for cobalt iron alloys with up to 50% cobalt. Its between 35 and 50% cobalt containing alloys have a low magnetocrystalline anisotropy, and the lowest values occur in the range of about

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Telephone (02 11) 32O8 58 Telegrams Cuatopat

50% cobalt. As a result, inductions are high at low Field strengths achieved. It should be noted, however, that as the cobalt content of the alloy is increased to a level that is above about 35% and up to about 80% by weight - with a corresponding decrease in the iron content - the alloy is an atomic one Order is subjected. Hence, cobalt iron alloys with a high cobalt content like the 50% cobalt iron alloy are quite good brittle, so that cold working is only possible after drastic quenching, which leads to high production costs.

While e subject for alloys containing less than 35% of cobalt, which no atomic ordering, a significant ductility can be observed, the high induction values for low field strength of this alloy have had probably never seen because of its high positive anisotropy. However, the improved ductility makes the alloys containing between about 5 and about 35% cobalt quite attractive in terms of economical manufacture.

Previously contained commercially available alloys on an iron basis about 27% cobalt. However, these alloys were - albeit in terms of overall saturation induction value showed a certain improvement - nonetheless deficient in that they were only low at low field strengths Exhibited inductions. In this respect, this material has only found limited use where it was designed to be close to the saturation value to work. While the presence of between about 5 and about 35% cobalt in iron leads to improved saturation values, could It has been found in connection with the present invention that grain alignment can be brought about by suitable machining where the high induction values are achieved at low field strengths without the coercive force or saturation induction values to affect. The inventive method for producing BEZW. Treatment of iron-cobalt alloys leads to results that are reflected in the observed magnetic properties.

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A method for producing iron-cobalt alloys is according to the invention characterized in that an alloy with between 5 and 35% by weight of cobalt, up to 3% by weight of the volume resistivity improving element, remainder iron with indefinite amounts of traces of contamination, melted and their sulfur content set, the alloy material thus obtained brought to an intermediate dimension by tub machining, the brought to an intermediate dimension Material subjected to an annealing treatment, the annealed material in one or more steps by cold working is brought to a desired final dimension, with at least a reduction by means of the last of the cold working steps of the cross-sectional area between 40 and 75% is effected, and that thereupon at a temperature in the range between 800 ° C and the A temperature is annealed, so that the high grain volume of the (110) fooiJ texture in Miller indices by primary recrystallization and normal grain growth is produced.

The first step of hot working the alloy material can be at a temperature between 1000 ° C and 1100 ° C under setting a desired intermediate dimension. In principle, any hot working process is sufficient, as this is not the case This is a critical point in the process, however, preference should be given to rolling. Preferably the final heat treatment occurs in a protective atmosphere such as an atmosphere of essentially pure hydrogen with a dew point less than about -40 ° C.

The invention also encompasses an alloy material with improved magnetic properties, between 5 and 35% cobalt, up to 3% of an element which improves the volume resistivity and the rest of which contains iron with indefinite amounts of traces of contamination and which is characterized in that it has a primary recrystallized grain structure in which a majority of the grains (110) texture and a majority of the aligned grains with the cube edges of their crystal lattices within an angle of 10 ° of the [ooi ^ -Vialzrichtung are aligned. To the elements which can cause an increase in volume resistivity,

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include chromium, silicon and manganese in amounts up to 2, 3 and

Within the broad chemical analysis set forth above, an embodiment with between 8 and 20% cobalt, from 0.5% to

2% silicon, a sulfur content of less than 0.005%, the remainder iron with indefinite amounts of traces of contamination is a preferred one Composition. Another preferred composition contains cobalt in the range between 20 and 30%, chromium in the range between 0.25 and 1%, less than 0.005% sulfur, the remainder essentially iron with the normal impurities. Outstanding Results were obtained where the cobalt content was kept within a range between 26.5% and 28%, at one Chromium content between 0.25 and 0.75%, less than 0.002% sulfur, the remainder iron with undetermined amounts of traces of contamination. This latter composition range has improved magnetic properties in terms of a high saturation value and high inductions at low field strengths, so that an excellent combination of magnetic properties is obtained.

Excellent magnetic materials can also be achieved if the cobalt content is within the range between 10 and 18% cobalt is kept at 0.5% to 2.0% silicon, less than 0.0025% sulfur, the remainder being essentially iron with indefinite amounts Impurities. This latter alloy has a greater resistivity in terms of silicon content and slightly lower saturation induction values, but the degree of alignment is still excellent, giving it an excessively high B value gives what not only for the degree of alignment, but also for the achievement of high inductions at low field strengths is a representative measure. As a result, make the different Combination / magnetic properties that can be achieved for the individual areas outlined above, in connection with the simplified treatment to achieve these desired results compared to the alloys of the invention commercially available oriented 3% silicon-iron of economic interest.

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· ■ 5 ""

It can be observed that the alloys according to the present Invention should be kept under control with regard to their sulfur content. The ability of the majority of the grains that Adopting the required degree of alignment presumably depends on the limitation on the initial sulfur content of the melt. As As explained in more detail below, there are no special requirements when processing the alloy into the product with the desired final dimension desulfurizing heat treatments carried out. Experimental test values currently available seem to indicate that a maximum sulfur content of about 0.05% can be tolerated, although less than 0.0025% is preferred give is. Excessively good results have been obtained where the sulfur content is reduced to a value of not more than 0.002% could be restricted.

Unless silicon is deliberately added as an alloying element, for example, if the cobalt content is kept within the range between about 20% and about 35%, it is desirable to keep the silicon content at a value of less than 0.25%. While silicon is known to improve volume resistivity, other elements such as Chromium, vanadium, aluminum, titanium and molybdenum are found to be more effective proven as long as the cobalt content is in the range between 20 and 35%. As a result, silicon is preferred as an alloying element only added where the cobalt makes up less than about 20%. Any element that is soluble and does not form a second phase, improves volume resistivity. Care must be taken, however, that the other properties do not turn out to be harmful Way to be affected. In the same sense, it was also found that the manganese content is preferably at a value of less than about 0.50% remains, although that is not absolutely necessary and is not critical * However, as far as silicon as an alloy component is added, for example in connection with a cobalt content between 8 and 20% to improve the resistivity the manganese levels remain fairly low, nominally around 0.05%.

The alloy can be used during normal processing of the alloy

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gen to the material with the final dimension of a decarburizing annealing however, the carbon content is preferably kept to less than about 0.030%, with an equivalent low oxygen content and the rest of the other impurities present in undetermined amounts. Typical values for these elements, about 0.003% oxygen, about 0.05% manganese, about 0.1% silicon, the remainder being essentially iron. Such Values of undetermined amounts of impurities can be determined by vacuum induction melting obtained, but other melting processes can be used with equal success.

The alloy having the desired composition is subjected to a hot working process and one or more cold working processes subjected in order to reduce the alloy material to the thickness corresponding to the desired final dimension. In this In this regard, it has been found that good results can be obtained when the alloy is hot worked, such as through, in ingot form Rolling at a temperature in the range between about 1000 ° C and about 1100 ° C. The material will work in this temperature range any intermediate dimension desired, hot machined to about a thickness of between 1.9 luid 3.8 mm. From the specified intermediate value for the rolling thickness, deviations are possible depending on the desired final thickness. In other words, the intermediate value for the thickness is selected with a view to the subsequent reduction in thickness by cold rolling or the final dimension.

Following hot working at a temperature in the range between 1000 ° C and 1100 ° C, the alloy is at a temperature for a period of about 10 minutes to about 60 minutes hot worked in the range between about 600 and 900 ° C. A hydrogen atmosphere is favorably used in this heat treatment introduced, for example, with a hydrogen atmosphere a dew point of more than about -40 ° C in order to decarbonize the material. In some cases it is desirable after recruitment of the intermediate value for the thickness to ensure decarburization, and typical annealing times of about 15 minutes at about 700 ° C in a hydrogen atmosphere with a dew point of about 15.6 ° C

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effect removal of approximately half of the carbon content remaining in the material following hot working. However, it is also possible to carry out the decarburizing heat treatment until immediately before the final heat treatment is carried out to delay or to switch on in every other step in between. After the decarburizing annealing it will Material pickled or descaled in preparation for cold working.

Cold working takes place in one or more operations, preferably in two steps. However, it has been found that it is necessary, at least with the final cold working step, in which the material is brought to its final dimensions, for a reduction in cross-sectional area between about 40% and about 75% to care. In this connection it has been observed that if the reduction in cross section is only less than about 40% matters, no sharply delimited (110) £ ooi] texture is obtained as with at least a 40% reduction in cross-sectional area. With cross-sectional area reductions of more than 75%, there is no pronounced impairment of the final texture, however, deterioration has been observed to some extent and the degree of recrystallization may be somewhat affected will. As a result, it has been found desirable to reduce the cold reduction to final dimensions to a value between about 40% and about 75%, with excellent results being obtained as far as the final cold reduction is between about 50 and was about 60%.

In this connection it should be noted that the initial cold reduction, if more than one cold reduction step is provided, it can be carried out by means of hot / cold working. D. that is, the material can be at a temperature above ambient but at a temperature below that temperature be heated, during which spontaneous recrystallization takes place during processing. Thus it finds, albeit the material is heated to a value well above room temperature, cold working takes place, which is why

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was designated "lferm- / cold ^H editing. In this regard, it was also found that when the intermediate dimension is mm after hot working, for example, 2.5, the hot rolling at a temperature in the range between about 200 ° C and about 300 ° C can be done to bring the material to a thickness of about 1 mm, whereupon the material is cooled to ambient temperature and then further cold rolled to about 0.63 mm Cold rolling step of about 75% of the cross-sectional area.

In all cases where the material has more than one cold working step is exposed, an intermediate anneal is preferably switched on, which lasts up to about 2 hours, at one Temperature between 700 and 900 ° C., for example more than about 800 ° C. Such an intermediate annealing is preferably carried out in an atmosphere of dry hydrogen, d. H. , a hydrogen content with a dew point of less than -40 ° C.

After such an intermediate annealing, the material is finished to size cold-worked, with this cold-working to the finished size typically reducing the cross-sectional area by 40 to 75% and excellent results have been obtained where the cold reduction is limited to between about 50 and 60% became. The processing does not only lead to a removal overall about half of the original carbon content, rather the material is also reduced to the finished size, whereupon the material is subjected to a final high temperature heat treatment to get the desired amount of aligned grain texture. In this context it was found that annealing the material at a temperature in the range between about 800 ° C. and the A. temperature for about 12 hours and about 72 hours in a hydrogen atmosphere with a dew point of less than -40 ° C, with subsequent furnace cooling, leads to an excellent degree of grain alignment, which by means of a primary Recrystallized grain structure was achieved, which has experienced normal grain growth. It was found that the

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Alignment textures were more pronounced as far as the material was concerned was quickly heated to a temperature of about 800 ° C with the pertigmass. As a result, the preferred treatment method comprises a strip anneal for 5 minutes at 800 ° C, followed by a final box anneal at a temperature in the range between 800 ° C and the A, temperature.

The invention is hereinafter referred to in connection with the following Examples explained:

Example I.

Table I below gives the chemical composition a number of batches made in accordance with the present invention in conjunction with a commercially available material Based on iron and about 27% cobalt content were produced and investigated. The latter material, however, has been treated using current commercial procedures.

Table I - Chemical Composition (Wt%)

alloy % Co % Cr % Mn % S % C % 0 M 849 27.5 - 0.15 0.008 0.015 0.0033 M 850 27.5 - 0.15 0.011 0.014 0.0030 M 851 27.5 - 0.15 0.021 0.013 0.0023 M 852 27.5 - 0.15 0.001 0.022 0.0031 M 853 27.5 0.59 0.15 0.001 0.010 0.0019 commercially
27% Co-Pe 27.6 0.59 0.37 0.009 0.015 0.0005

These alloys were made from the aforementioned compositions High purity raw materials are melted, allowing a largely accurate control of elements such as sulfur, carbon and Oxygen was guaranteed. After vacuum induction melting Each of the alloy ingots was processed into sheets or ribbons in the following way:

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Hot rolling at 1050 ° C to 2.5

mm;

Anneal for 15 minutes at 700 ° C in hydrogen;

pickling or descaling; Hot rolling at 260 ° C to 1.0 mm, then cold rolling to 0.625 mm; Annealing for 1 hour at 900 ° C in dry hydrogen; and

Cold rolling to a finished dimension of 0.3 mm.

The above procedure removes about half of the original carbon while not significantly changing the other additions, including sulfur. The cut material was cut into Epstein strips in the direction of rolling. In addition, a 2.5 cm diameter torque disk for each alloy was placed at 900 ° for 48 hours C annealed in dry hydrogen and then cooled in the furnace.

See Table II below for the DC magnetic properties for each alloy reproduces.

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sample Apex
moment
(erg / cm ^J ) - 11 - ^B 10
(G) 2307929 M 849 64,700 Magnetic 18,400 Table II - M 850 53,400 moment
behaves
nis properties 17,300 ^B 100
(G) M 851 44,100 0.53 ^H c
(Oe) 17,200 22,700 M 852 131,000 0.61 1.03 19,300 22,0OO M 853 138,000 0.42 1.36 19,600 22,100 commercially
27% Co-Fe
(inexplicable
judges) 0.45 1.59 16,100 23,100 commercially
3% Si-Fe
(aligned
tet) 167,000 0.37 0.60 18,300 22,900 0.57 21,100 0.34 1.70 19,800 0.11

To complete the comparison, data is also included for a typical commercial batch of a 3% unaligned silicon steel and a 27% cobalt-iron alloy (unaligned). In evaluating the data presented in Table II, it should be remembered that the "peak moment" values in the table represent the average of the absolute values of the large peaks in the curve. The moment ratio represents a ratio of the absolute values of the small peaks to the large peaks for a given curve. Since the commercially-treated 27% -Kobaltmaterial had no measurable peak torque and a B _1Q value of only 16,100 Gauss, these values clearly indicate that the grain texture is random in the processed commercially or conventionally material substantially.

On the basis of the instantaneous values or induction values at 10 Oersteds compiled with Table II, it can be seen that significantly higher B values were achieved for the individual compositions. However, the compositions with the lowest sulfur content, ie, batches M 852 and M 853, had particularly high B _1Q values, in conjunction with peak moment values close to

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Value for the 3% silicon iron, which has a high level of (110) [has ooij alignment for commercially available material.

This can be shown more clearly with reference to FIG. 1, in of the diagrams of the moment values as a function of the angle between the field and the rolling direction in degrees for a highly oriented 3% silicon iron as well as for the alloys M 853 and M 849 are superimposed. It can therefore be derived from the value for M 853 see that by reducing the sulfur content to a critically low level and treating the material as further shown above a strong approximation of moment curves that come close to those of the commercially available 3% silicon iron, he follows. By comparing the saturation values in Table II, i.e. H. the induction values for the field strength of 100 Oersted / it can be clearly seen, however, that much higher saturation induction values in conjunction with the cobalt iron alloys, at overall due to the orientation of the material improved magnetic properties.

Referring now to Figures 2-6, the macro photographic Reproduce recordings of alloys as listed here and given in Table I with their structure. These macro photographs have a magnification factor of 20 after annealing the cobalt iron alloy sheets for a period of 48 hours at a temperature of 900 ° C and show a strong relationship between the sulfur content and the final grain size. From Figures 2 to 6 it can be seen that the low sulfur levels result in a large grain size with normal grain growth; H. the end a primarily recrystallized microstructure and not as a result of secondary recrystallization and grain growth. These results as well as the shorter annealing times for batches M 852 and M 853 show that the degree of (110) [pol] texture through primary Grain growth in alloys with low sulfur content is increased. This is in direct contrast to the development a similar oriented texture in 3% silicon iron, where high levels of controlled sulfur result in texture formation secondary grain growth are required. So let the alloy

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M 852 and M 853 stanchions have the additional favorable point of view recognize that the cobalt iron alloys with low sulfur values have low coercive force values. In addition, it seems it is that the addition of chromium to these cobalt iron alloys is the Seems to aid texture formation to some extent while increasing volume resistivity.

Another batch of cobalt iron alloy was melted to essentially the same composition as batch M853. This batch was designated as batch M 903 and im essentially treated under the same conditions as batch M 853, with the following exception. After annealing during a The material was cold-rolled to the final thicknesses of 0.28 mm and 0.30 mm for an hour at 900 ° C. with an intermediate value of 0.6 mm.

Reference is now made to Table III for the magnetic properties of Lot M 903.

Table III - Magnetic Properties Vertex- moment'- _H _ _n Alloy strength moment behavior- ^M c 10 100

sample (mm) (erg / cnr) never (Oe) (G) (G)

M 903 O, 24 180,800 0.38 0.35 21,200 23,700 M 903 0.30 123,700 0.36 -

A texture analysis of the distribution of the white ^{1 areas was} carried out on material samples from batches M 852 and M 903, batch M 903 having a final thickness of approximately 0.28 mm. It was found that 85 Vo 1% of the grains had the (HO) - and 7 vol% the (100) texture, the (HO) grains having crystal lattices, the cube edges of which for 80% of the grains were within 10 ° of [ poij direction. When a deviation from the [poij or rolling direction was measured within 15 °, it was found that the edges of the crystal lattices of 88 tons of the (110) grains were within this limit.

The batch M 852 was a final cold reduction from straight

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SO% granted »βο that as a result they are not as high in texture as formed the batch M 903 rolled to a thickness of 0.28 mm. Actual measurements of Batch M 852 showed that 61 full of Grains had the (110) texture while 16% had the (100) texture. Furthermore, 58% of the cube edges of the crystal lattices deviated less than 10 t from the [oo Ij -direction, and 68% of the grains were within 15 ° of the (poij -direction.

For each of the above cases, the texture formed as a result primary recrystallization and normal grain wax turns out. In all cases the presence of the (100) [oof] texture does not result in away from the magnetic properties of the alloy containing the predominant texture (110) [ooi].

These values appear to indicate that a slightly higher level of final cold reduction leads to an improvement in texture and that extremely high induction values are obtained. When the B _1Q values as well as the peak moment values for the batch M 903 in the O _# 28 mm stage are compared to the commercial grade 3% silicon steel reported in Table II, it is clear that for the batch M 903 has a higher hatred of (110) [ooi] texture than was obtained for the commercial 3% silicon steel. The peak torque values are higher, the B ^ Q values are higher and, as expected, the saturation values are clearly in the vicinity of the theoretical maximum.

Example II

Another series of batches was investigated in which the Sulfur content was kept within very low limits, so that the sulfur content was less than 0.001% by weight. It will be in In this connection, reference is made to Table IV below which gives the chemical composition of the three batches which were tested.

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Table IV - Chemical Composition (wt%)

alloy 838 % Co % Cr % Mn % Si % C. M. 839 27 , 0 0 , 59 <0 , 02 <0 , 03 0 , 004 M. 840 26th ,8th 0 , 59 0 , 43 <0 , 03 0 , 005 M. 26th ,8th 0 , 59 0 , 43 0 , 13 0 , 005

% S

% 0

Both the disk samples for the moment measurements and the Epstein samples were cut out of the material and 48 Annealed for hours at 900 ° C in dry hydrogen.

Further reference is made to Table V below which lists the magnetic properties of the alloys.

Table V - Magnetic Properties

Peak moment
Alloy (erg / cm)

M 838
M 839
M 840

81,500
90,700
81,300

Moment ratio
nis

0.52
0.48
0.41

^H c
(Oe)

0.62 0.89 0.41

10

19,100
18,900
19,000

^B 1OO (G)

22,700 22,700 22,800

From the test results presented in Table V it can be seen that high B _Q values were obtained, indicating a high degree of (110) jjDO1] alignment. The saturation values for the alloys were also very acceptable, although the peak moment values were somewhat lower than for the better materials discussed above. It is believed that the thicker hot rolled sheet material, which results in much higher intermediate cold reductions, will give somewhat lower peak moment values. Accordingly, the aim is to limit the cold reduction brought about in the individual stages to a value which lies within a range between approximately 40% and approximately 75% of the cross-sectional area.

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Example III

Additional cobalt levels were investigated to determine the relative level of cobalt that is effective to provide the improved induction levels to achieve that of achieving the required level of (110) £ ooi3 ~ alignment in a primarily recrystallized Micro-structure. In this regard, reference is made to Table VI below for the nominal composition of two alloys made and tested in accordance with the present invention, referring to it should be noted that the alloys given in Table VI contain 18% cobalt and 10% cobalt, respectively. It was a corresponding proportion of silicon of 1% or 2% added in order to achieve the improved volume resistivity. In these batches the sulfur content was adjusted so that the value is below about 0.003%.

Table VI - Nominal Chemical Composition Alloy% Co% Si% Mn

M 883 18 1.0 0.05

M 887 10 2.0 0.05

The alloys were then treated as follows: hot rolling at 1050 ° C to 2 mm; pickling or descaling;

Glow in dry hydrogen at 850 ° C for 5 hours;

Cold rolling to 0.6 mm;

Glow in dry hydrogen at 850 ° C for 5 hours;

Now cold-roll to a final size of 0.27.

After cold rolling to final size, the alloys were about 5 minutes strip annealed at 850 ° C in moist hydrogen and then annealed for 40 hours at 940 ° C in dry hydrogen.

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_ ₁₇ _ 7307929

The strip annealing was carried out with a view to decarburization, and the final annealing took place at a temperature close to the A.

C X

door, but below this A temperature.

Further reference should be made to Table VII which lists the magnetic Specifying properties for the alloys of Table VI.

Table VII - Magnetic Properties

Vertex- moment- "

moment _ behavior- c 10 1OO sample (erg / cm) nis (Oe) (G)

M 883 106,700 _{Q 44} 0.368 18,500 21,7OO M 887 121,300 0.45 0.275 18,000 20,9OO

The instantaneous value suggests a high degree of (110) (pol) texture. The 10% cobalt sample seems to be a bit more textured, however, the 18% cobalt alloy has higher saturation due to its higher saturation a higher induction value. These samples showed only primary recrystallization and normal grain growth. In other investigations were for similarly treated alloy compositions much lower torque values are obtained with sulfur additives of 0.01%. Likewise, seem slowly to a final annealing temperature heated samples give poor results.

From the above examples it can be seen that a higher degree of (110) [pol] texture is carried over into cobalt iron alloys a wide range of cobalt, manganese, silicon and chromium components can be obtained by primary recrystallization and normal grain growth. The course of treatment is clearly important, and so is it it should be noted that the final annealing is below the alpha-ZGamma transition temperature must be kept, which is about 95O ° C, or, more precisely, the final annealing must be at a Stay at the maximum temperature that is below the A temperature. Such monitoring of the sulfur content will be carried out by primary recrystallization and grain growth in (110) [pol] -textured alloys. Let accordingly transformers and devices with rotating magnetic core

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- X Ö ~

Such as motors and generators that use this material make what results in significant economic advantages in the manufacture of both the alloy and the devices.

Patent claims:

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Claims (23)

Patent claims 1. A process for the production of iron-cobalt alloys, characterized in that an alloy with between 5 and 35% by weight Cobalt, up to 3% by weight of a volume resistivity enhancer Element, remainder iron with indefinite amounts of traces of contamination, melted and adjusted its sulfur content, the alloy material thus obtained is brought to an intermediate dimension by hot working, the brought to an intermediate dimension Material subjected to an annealing treatment, the annealed material in one or more steps by cold working is brought to a desired final dimension, at least by means of the last of the cold working steps a reduction in cross-sectional area between 40 and 75% is effected, and that thereupon at a temperature in the range between 800 ° C and the A. Temperature is annealed, so that the high grain volume of the (110) [boI ^ texture in Miller indices Generated by primary recrystallization and normal grain growth. 2. The method according to claim 1, characterized in that the final alloy contains less than 0.005% sulfur. 3. The method according to claim 2, characterized in that the final alloy contains less than 0.002% sulfur. 4. The method according to claim 1, 2 or 3, characterized in that the cross-sectional area of the cold-worked material in the Range between 40% and 75% is reduced in one step. 5. The method according to one or more of claims 1-4, characterized in that the initial cold working at a temperature of up to 300 ° C is carried out. 309836 / 08ÖÜ 6. The method according to one or more of claims 1-5, characterized characterized in that between each cold working step an intermediate anneal at a temperature between 700 and 900 ° C is switched on. 7. The method according to claim 6, characterized in that the intermediate annealing takes place in a decarburizing atmosphere. 8. The method according to claim 7, characterized in that the decarburizing atmosphere is hydrogen with a dew point of is at least 4.4 ° C. 9. The method according to any one of claims 1-8, characterized in that that all annealing processes are carried out in a hydrogen atmosphere. 10. The method according to one or more of claims 1-9, characterized in that the alloy composition is up to Contains 2% chromium, up to 1% manganese and up to 3% silicon. 11. The method according to claim 10, characterized in that the alloy to an intermediate dimension between 0.2 mm and 0.38 mm Thickness when machined and after cold working at one tempe; will. Annealed temperature in the range between 850 ° C and 950 ° C 12. The method according to claim 10 or 11, characterized in that the alloy composition is cobalt in an amount of Contains 20% to 30% and chromium in an amount of 0.25% to 1.0%. 13. The method according to one or more of claims 1-12, characterized characterized in that the alloy material obtained is hot worked at a temperature between 1000 ° C and 1100 ° C will. 309836/0890 '/ 307929 14. The method according to one or more of claims 1-13, characterized characterized in that the alloy material brought to an intermediate dimension at a temperature between 600 and 900 ° C is annealed. 15. The method according to one or more of claims 1-14, characterized characterized in that the cross-sectional area of the cold worked alloy at least in connection with the latter Reduction to the final dimension between 50 and 60% is reduced. 16. According to one or more of claims 1-15 produced iron cobalt alloy, characterized in that it is a has a primary recrystallized grain structure in which a majority of the grains have (110) texture and a majority of the aligned grains with the cube edges of their crystal lattices within an angle of 10 ° of the £ ooi ^] -Wal ζ direction are aligned. 17. Alloy according to claim 16, characterized in that the sulfur content is less than 0.05%. 18. Alloy according to claim 17, characterized in that the sulfur content is less than 0.002%. 19. Alloy according to claim 16, 17 or 18, characterized in that that the chromium content up to 2%, the manganese content up to 1% and the silicon content makes up to 3%. 20. Alloy according to claim 19, characterized in that the cobalt between 8 and 20% and the silicon between 0.5 and 2%. 21. Alloy according to claim 19, characterized in that the cobalt between 20 and 30% and the chromium between 0.25 and 1.0%. 309836/0890 22. Alloy according to claim 21, characterized in that the proportion of cobalt between 26.5% and 28% and the proportion of Chromium makes up 0.75%. 23. Alloy according to claim 19 or 2O, characterized in that that the cobalt content is between 10% and 18%. KN / hs 3 309836/0890 Blank page