EP0407608B1 - Magnetische nickel-eisen legierung mit hoher permeabilität - Google Patents

Magnetische nickel-eisen legierung mit hoher permeabilität Download PDF

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EP0407608B1
EP0407608B1 EP90901881A EP90901881A EP0407608B1 EP 0407608 B1 EP0407608 B1 EP 0407608B1 EP 90901881 A EP90901881 A EP 90901881A EP 90901881 A EP90901881 A EP 90901881A EP 0407608 B1 EP0407608 B1 EP 0407608B1
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nickel
alloy
magnetic
permeability
boron
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EP0407608A4 (en
EP0407608A1 (de
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Tadashi Inoue
Masayuki Kinoshita
Tomoyoshi Ohkita
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JFE Engineering Corp
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NKK Corp
Nippon Kokan Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14708—Fe-Ni based alloys

Definitions

  • This invention relates to a nickel-iron base magnetic alloy having high permeability and more particularly to a nickel-iron base magnetic alloy having improved magnetic properties, such as permeability and shielding properties in a direct current and low frequency region.
  • a nickel-iron base magnetic alloy equivalent to JIS PC is a magnetic material which now finds very wide applications such as magnetic head cases and various cores, transformation cores and various magnetic shielding materials.
  • Such a PC permalloy is characterized by high permeability and low coercive force, and examples of the PC permalloy which has been put to practical use up to now include 80 % nickel - 5 % molybdenum - iron (: superalloy) and 77 % nickel - 5 % copper - 4 % molybdenum - iron (: Mo, Cu permalloy).
  • the permeability level obtained by the above described alloys is usually 150,000 for the initial permeability (hereinafter refferred to as “ ⁇ i ”) and about 300,000 for the maximum permeability (hereinafter reffered to as “ ⁇ m ").
  • JP-A No. 63-149361 proposes to conduct deboronization during magnetic annealing of a material comprising an alloy of the above-described component system and boron added thereto for the purpose of improving the hot workability during manufacture of the magnetic material.
  • the described component system is expensive because it contains about 80 wt.% of nickel.
  • the component system has been thoroughly reconsidered and development has been made on a technique described in JP-B2 No. 62-13420 wherein high initial permeability has been attained by decreasing the content of nickel and adding, instead of nickel, copper and manganese more inexpensive than nickel; and a technique described in JP-A Nos. 63-247336 and 63-247339 wherein a suitable amount of aluminium is added in addition to the technique described in said JP-B2 No. 62-13420 for the purpose of decreasing inclusions and enhancing the magnetic properties.
  • the maximum ⁇ i values of the alloys proposed in said JP-A Nos. 63-247336 and 63-247339 are on a level as high as 426,000.
  • this technique is characterized by adding 1 to 4 wt.% of silicon to an ordinary molybdenum superalloy to attain satisfactory permeability even at a relatively low magnetic annealing temperature, e.g., at about 1,030°C or below.
  • the level of direct current magnetic properties after heat treatment (1,100°C ⁇ 3 hr) in a hydrogen atmosphere as the final step is, e.g. 100,000 at the highest in terms of ⁇ i , which renders the alloy unsuitable for applications where a higher level of magnetic properties is required.
  • JP-A No. 62-227054 the cost becomes high because chromium is newly added to the ordinary Ni-Fe-Mo base or Ni-Fe-Mo-Cu base component.
  • the proposal described in JP-A No. 62-227053 has, besides a problem of high cost derived from the addition of chromium, a problem on manufacture of a magnetic material that the hot workability becomes very poor due to the manganese level (must be made to 1.2 ⁇ 10 wt.%) higher than the ordinary level.
  • Boron is added in both the described proposals.
  • the addition of boron in this case is conducted for the purpose of improving the hot workability and punchability, and mere addition of boron intended in the above proposals brings about no significant improvement in the magnetic properties and sometimes deteriorates the magnetic properties.
  • JP-A No. 63-149361 the magnetic properties are improved by the deboronization treatment.
  • the level of the magnetic properties after treatment is 75,000 at the highest in terms of ⁇ i , i.e., the same as that obtained in the ordinary Ni-Fe-Mo-Cu base alloy. Therefore, this technique is unsuitable for applications where a higher level of magnetic properties is necessary.
  • the technique described in JP-B2 No. 62-13420 and JP-A Nos. 63-247336 and 63-247339 can provide a permalloy having a high ⁇ i value, but has a problem of substantial lowering in the hot workability during manufacture of the magnetic material due to an increase in the manganese and copper contents.
  • the saturation magnetic flux density of the alloy prepared in this proposal is, e.g., 5,000 gauss in terms of B10 (magnetic flux density at 10 oersted), namely, lower than that of the superalloy and Mo, Cu permalloy, namely, 7,000 to 8,000 gauss in terms of B10.
  • the magnetic flux in the alloy is unfavorably saturated in a lower external magnetic field than that in the case of the superalloy and Mo, Cu permalloy, which renders the alloy unsuitable for use a shielding material in a place where the external field is relatively high.
  • JP-A 1-100232 has a problem of deterioration of workability and lowering in the production property of the magnetic material due to addition of a large amount of silicon. Further, in this technique, the shielding performance is on a necessary level at 50Hz but disadvantageously slightly poor in a direct current.
  • the inventors of the present invention have made further studies on the effect of major components, such as nickel, molybdenum, copper and iron, on the magnetic characteristics with a view to substantially improving the magnetic properties, such as permeability, and shielding performance in a direct current and a low frequency region and further enabling the magnetic annealing for attaining the properties on the same level as that in the case of the background art to be conducted at a temperature of about 100 °C lower than the conventional annealing temperature, and conducted experiments and research on the relationship between the properties obtained in the studies and the components with extension to the boron-added system, which has led the completion of this invention.
  • major components such as nickel, molybdenum, copper and iron
  • the improvement in the magnetic properties intended in this invention can be attained under control of the level of impurities in the alloy, and the reasons for limitation of the contents (wt.%; hereinafter referred to simply as "%") of phosphorus, sulphur, oxygen, nitrogen and carbon are as follows.
  • Phosphorus is an element which is detrimental to the hot workability of high Ni-Fe alloy intended in this invention and weakens the tendency of forming a cubic aggregate structure during final annealing with hydrogen.
  • the upper limit of phosphorus was set to 0.010 %.
  • the lower limit is preferably 0.0010 % from the viewpoint of economy of ingot.
  • Sulfur is detrimental to the hot workability and very deterimental also to the magnetic properties because it hinders the grain growth during final annealing with hydrogen through formation of a sulfide and brings about a reduction in the particle diameter after annealing, so that no improvement in the permeability is attained.
  • the sulfur content is more preferably 0. 0005 % or less from the viewpoint of a further improvement in the permeability in a direct current and an alternating current.
  • the upper limit of the nitrogen content was set to 0.0010 % because when the content exceeds 0.0010 % the magnetic properties remarkably deteriorates for the above-described reason.
  • the nitrogen content is more preferably 0.0005 % or less from the viewpoint of a further improvement in the permeability in an alternating current.
  • Carbon is an element which is detrimental to the magnetic properties because it exists as an interstitial element in an alloy intended in this invention and when the amount of carbon is large the permeability lowers.
  • the upper limit of the carbon content was set to 0.020 % because the magnetic properties remarkably deteriorates for the above-described reason.
  • the object of the present invention cannot be attained without optimization of amount of addition of nickel, molybdenum, copper, iron and boron under control of impurity elements and control of the balance of the amounts of the components in a particular range. More specific description thereon will now be given.
  • Nickel provides high magnetic properties and high shielding properties intended in the present invention when the content is 77.5 to 79.5 %.
  • the lower limit and upper limit of the content was limited to 77.5 to 79.5 %, respectively, because when the content is less than 77.5 % or exceeds 79.5 % the permeability lowers.
  • Molybdenum provides high magnetic and high shielding properties intended in the present invention when the content is 3.8 to 4.6 %.
  • the molybdenum content is less than 3.8 % or exceeds 4.6 %, no improvement in the permeability can be attained, which makes it necessary for the content to be 3.8 to 4.6 %.
  • Copper serves to markedly improve direct current magnetic properties, the effective permeability in an alternating current and the squareness (Br/Bm) in an alternating current (50 Hz) of an alloy falling within the scope of the present invention in the presence of boron which will be described later.
  • the above-described effects can be attained when the nickel and molybdenum contents are 77.5 to 79.5 % and 3.8 to 4.6 %, respectively, and the optimal copper content is 1.8 to 2.5 %.
  • the copper content was limited to 1.8 to 2.5 % because when the content is less than 1.8 % no improvement in the properties by copper can be attained while when the content exceeds 2.5 % the properties deteriorate.
  • manganese is an element which has an influence on the magnetic properties of an alloy intended in this invention. Although it is possible to attain high permeability intended in this invention even when the manganese content is 1.10 % or less, the hot workability unfavorably deteriorates when the content is less than 0.10 %. Therefore, the lower limit was set to 0.10 %.
  • Boron is an element necessary for attaining high permeability intended in the present invention.
  • the object of the present invention can be effectively attained when is 0.0005 to 0.0070.
  • the value is less than0.00005 % no improvement in the permeability can be attained while when the value exceeds 0.0070 % the permeability lowers. Therefore, the upper and the lower limits of were specified to 0.0005 % and 0.0070 %, respectively.
  • Figs. 1 to 4 are diagrams respectively showing the initial permeability, the degree of shielding, the effective permeability at 1 kHz and the squareness at 50 Hz obtained in each material under test, wherein the parameter specifying the balance of said components (this parameter is represented by X and 3.3 ⁇ 2.02 ⁇ [Ni] - 11.13 ⁇ [Mo] - 1.25 ⁇ [Cu] - 5.03 ⁇ [Mn] 2.13 ⁇ [Fe] ⁇ 3.8 is plotted as ordinate and the amount of addition of boron as abscissa.
  • All the materials under test shown in Figs. 1 to 4 have nickel, molybdenum, copper, manganese, boron, phosphorus, sulfur, oxygen, nitrogen and carbon contents falling within the scope of this invention and were prepared by repeating cold rolling and annealing after hot working to prepare a thin sheet sample having a thickness of 0.5 mm and punching the sheet to prepare JIS-ring samples each having an outer diameter of 45 mm and an inner diameter of 33 mm, heat-treating the samples at 1,100 °C for 3 hr in a high-purity hydrogen stream atmosphere purified by passing it through a palladium film, cooling the samples from 1,100 °C to 650 °C at a rate of 100 °C/hr and then allowing the samples to cool in a furnace.
  • the degree of shielding was determined by applying an external magnetic field (H0) of 500 milligauss by means of a helmholtz coil to a cylinder subjected to the same production history as that of the above materials and having a wall thickness of 0.5 mm, a diameter of 50 mm and a length of 200 mm in a direction normal to the axial direction of the cylinder and then measuring the internal magnetic field H1 at the center of the inside of the cylinder.
  • the figures (degree of shielding) in the drawing are each a value H0/H1. The measurement was conducted in a box subjected to magnetic shielding to such an extent that the influence of the earth magnetism is sufficiently negligible.
  • the effective permeability at 1 kHz was determined by measuring the inductance permeability at 5 millioersted through the use of a ring sample having a wall thickness of 0.35 mm subjected to the same magnetic annealing as that of the above materials, and the squareness at 50 Hz was determined from the Br to Bm ratio at a magnetic field of 0.1 oersted by making use of the same sample as that used for the measurement of the effective permeability.
  • Bm is the magnetic flux density within the material when an external magnetic field of 0.1 oersted is applied
  • Br is the magnetic flux density in the case where the external magnetic field is removed from the state subjected to application of an external magnetic field of 0.1 oersted. They are hereinafter referred to simply as "Br" and "Bm", respectively.
  • the initial permeability ⁇ i is as high as at least 350,000.
  • ⁇ i is on a level as low as less than 200,000.
  • ⁇ i is less than 200,000 and no improvement is attained if is less than 0.0005.
  • ⁇ i lowers.
  • the materials falling within the scope of this invention exhibit a high value of 300 or more which is higher than the degree of shielding of the materials outside the scope of this invention.
  • Fig. 3 is a diagram showing the results of measurement of the effective permeability.
  • the materials falling within the scope of this invention exhibits a value as high as at least 6,500 which is higher than the materials outside the scope of this invention.
  • Fig. 4 shows that in the squareness at 50 Hz as well, the materials falling within the scope of this invention exhibit a value as high as at least 0.90 which is higher than that of the materials outside the scope of this invention.
  • the present inventors have repeated studies with a view to further enhancing magnetic properties by making use of the above-described alloy of this invention and, as a result, have confirmed the fact that a further improvement in the initial permeability ⁇ i and the degree of shielding can be attained when the boron content at and near the austenite grain boundary of the alloy after heat treatment for enhancing the final magnetic properties is within a particular range. Specifically, Figs.
  • the ⁇ i was determined by repeating cold rolling and annealing after hot working to prepare a thin sheet sample having a thickness of 0.5 mm and subjecting the sheet to punching to prepare JIS-ring samples each having an outer diameter of 45 mm, an inner diameter of 33 mm, heat-treating the samples at 1,100°C for 3 hr in a high-purity hydrogen stream atomsphere purified by passing it through a palladium film, cooling the samples from 1,100 °C to 650 °C at a constant rate of 50 to 400°C/hr, allowing the samples to cool in a furnace and then measuring the ⁇ i value of the samples.
  • the result are shown in the relationship with the boron content at and near the austenite grain boundary.
  • the boron content at and near the austenite grain boundary was determined by cutting out a notched specimen mountable on a stage for the Auger observation from a sample subjected to the same hot working history as that of the thin sheet sample used for measurement of ⁇ i , adding electrolytic hydrogen to the specimen by the cathodic electrolysis, subjecting the specimen to embrittlement to conduct fracturing of grain in vacua, conducting analysis of components on 10 points of the resultant fracture of grain by Auger electron spectroscopy and averaging the data.
  • the unit is atm%.
  • the degree of shielding was determined by applying an external magnetic field (H0) of 500 milligauss by means of a helmholtz coil to a cylinder subjected to the same production history as that of the above materials and having a wall thickness of 0.5 mm, a diameter of 50 mm and length of 200 mm in a direction normal to the axial direction of the cylinder and then measuring the internal magnetic field H1 at the center of the inside of the cylinder.
  • the effective permeability at 1 kHz was determined by measuring the inductance permeability at 5 millioersted through the use of a ring sample having a wall thickness of 0.35 mm subjected to the same magnetic annealing as that of the materials, and the squareness at 50 Hz was determined from the Br to Bm ratio at a magnetic field of 0.1 oersted by making use of the same sample as that used for the measurement of the effective permeability.
  • ⁇ i value is improved when the boron content at and near the austenite grain boundary is 10 to 50 atm%.
  • the ⁇ i value is 480,000 or more when the boron content is 15 to 40 atm%.
  • the reason for the improvement in the ⁇ i value has not been elucidated yet, it is believed that the presence of a suitable amount of boron at the grain boundary changes the property of the grain boundary and this change has a favorable effect on magnetic properties, particularly property value, such as initial permeability, wherein easiness of movement of magnetic domain walls or easiness of rotary magnetization are required.
  • the boron content at and near the austenite grain boundary after magnetic annealing was specified to 10 to 50 atm% for attaining a combination of high ⁇ i value and a high degree of shielding with a relatively high effective permeability and a relatively high squareness.
  • the intended Ni-Fe alloy is poor in the hot workability.
  • addition of a minor amount of boron is often combined with addition of a minor amount of calcium.
  • Even when calcium is added an improvement in the initial permeability intended in this invention can be attained if the above-described characteristics features of this invention are satisfied.
  • incorporation of 0.3 % or less of silicon and 0.03 % or less of aluminium besides the above-described composition is permissible in this invention.
  • High Ni-Fe alloy of this invention and comparative alloys having a chemical composition shown in Fig. 1 were prepared in the form of an ingot by vacuum dissolution, subjected to hot working and descaling to prepare cold rolled materials. All the materials under test had a silicon content of 0.05 to 0.15 %. These materials were then cold worked and annealed to prepare thin sheet samples having a thickness of 0.5 mm and subjected to punching to prepare as samples JIS-rings having an outer diameter of 45 mm and an inner diameter of 33 mm.
  • Each sample was subjected to measurement of magnetic properties by heat-treating the samples in a high-purity hydrogen stream atmosphere at 1,100 °C for 3 hr, cooling the heat-treated samples from 1,100°C to 650 °C at a rate of 400 °C /hr, cooling the samples in a furnace and then measuring the magnetic properties.
  • the results of measurement of ⁇ i in terms of the permeability at 0.005 oersted are shown in Table 1 together with the results of measurement of the degree of shielding, effective permeability, squareness at 50 Hz, coercive force and magnetic flux density.
  • the degree of shielding was determined by applying an external magnetic field (H0) of 500 milligauss by means of a helmholtz coil to a cylinder subjected to the same production history as that of the above materials and having a wall thickness of 0.5 mm, a diameter of 50 mm and a length of 200 mm in a direction normal to the axial direction of the cylinder and then measuring the internal magnetic field H1 at the center of the inside of the cylinder.
  • the effective permeability at 1 kHz was determined by measuring the inductance permeability at 5 millioersted through the use of a ring sample having a wall thickness of 0.35 mm subjected to the same magnetic annealing as that of the above materials, and the squareness at 50 Hz was determined from the Br to Bm ratio at a magnetic field of 0. 1 oersted by making use of the same sample as that used for the measurement of the effective permeability.
  • the magnetic flux density and the coercive force were measured by making use of the same samples as those used for measurement of the initial permeability.
  • the magnetic flux density, B1000 is one when an external magnetic field of 1000 A/m is applied, and the coercive force is a strength of the magnetic field necessary for making the magnetic force zero when an external magnetic field of 1000 A/m is applied and then inverted.
  • Alloys Nos. 1 and 2 materials have carbon, phosphorus, sulfur, oxygen, nitrogen, boron, nickel, molybdenum, copper, and manganese contents all of which fall within the scope of this invention. They exhibits ⁇ i value as high as at least 350,000 and also exhibits a degree of shielding as high as about at least 300. Further, the effective permeability, squareness at 50 Hz and coercive force as well are on a level superior to that of the control examples.
  • Alloy Nos. 3 and 4 have carbon, phosphorus, sulfur, oxygen, nitrogen, boron, nickel, molybdenum, copper, and manganese contents falling within the scope of this invention and contain a minor amount of calcium added for improving the hot workability.
  • each property value is on substantially the same level as that of the above-described alloy Nos. 1 and 2. In other words, it has been confirmed that the effect of this invention can be sufficiently exhibited in the alloy containing a minor amount of calcium added thereto.
  • Alloy No. 5 has carbon, sulfur, oxygen and nitrogen contents reduced to a favorable level and exhibits property values higher than those of alloy Nos. 1 to 4.
  • the deterioration of the initial permeability during application of a face pressure of 392 kPa [4 kgf/mm2] as well is lower than that of the following control alloy Nos. 6 to 22 and 14 to 22, and it is apparent that the deterioration of characteristics against strain as well is smaller.
  • alloy material Nos. 6 and 7 respectively have nickel contents exceeding the upper limit and below the lower limit
  • alloy material Nos. 8 and 9 respectively have molybdenum contents exceeding the upper limit and below the lower limit
  • alloy material Nos. 10 and 11 respectively have copper contents exceeding the upper limit and the below the lower limit.
  • Alloy No. 12 has a manganese contents exceeding the upper limit
  • alloy No. 13 has a manganese content below the lower limit
  • alloy Nos. 14 and 15 respectively have boron content exceeding the upper limit and below the lower limit
  • alloy Nos. 16 to 20 respectively have carbon, phosphorus, sulfur, oxygen and nitrogen contents exceeding the scope of composition of this invention, and alloy Nos.
  • alloy 21 and 22 respectively have parameter X's exceeding the upper limit and below the lower limit specified in this invention. All of these material Nos. 6 to 21 under test except for alloy No. 13 are on a lower level of property value than that of the materials of this invention. As described above, alloy No. 13 has a manganese content below the lower limit specified in this invention. This material exhibits property levels comparable to these of the material of this invention but is remarkably inferior in the hot workability during manufacture of the sample.
  • Alloy Nos. 1 to 4 of this invention described in said Example 1 was cold rolled and annealed to prepare a thin sheet sample having a thickness of 0.5 mm and subjected to punching to prepare as samples JIS-rings having an outer diameter of 45 mm and an inner diameter of 33 mm. Further, a notched specimen mountable on a stage for the Auger observation was cut out from the same thin sheet sample.
  • the samples thus prepared were heat treated at 1,100°C for 3 hr, cooled from 1,100°C to 650 °C at different colling rates, cooled in a furnace and then subjected to measurement of magnetic properties and degree of shielding.
  • the boron content at and near the austenite grain boundary was determined by adding, after the above-described heat treatment, electrolytic hydrogen to the samples by the cathodic electrolysis for embrittlement, conducting fracturing of grain in vacua and conducting analysis of components on 10 points of the resultant fracture of grain by Auger electron spectroscopy and averaging the data.
  • Table 2 The results are summarized in Table 2.
  • material Nos. 14 to 16 under test of which the boron content at and near the austenite grain boundary falls within the range specified in claim 3 exhibit higher ⁇ i value and degree of shielding than those of material Nos. 13 and 18 under test of which the boron content at and near the austenite grain boundary is outside the range specified in claim 3.
  • material Nos. 19, 20, 22 and 23 under test of which the boron content at and near the austenite grain boundary falls within the range specified in claim 3 exhibit higher ⁇ i value and degree of shielding than those of material No. 24 under test of which the boron content at and near the austenite grain boundary is outside the range specified in claim 3.
  • the material Nos. 1 to 4, 8 to 11, 14 to 16, 19, 20, 22 and 23 under test of which the boron content at and near the austenite grain boundary falls within the range specified in claim 3 exhibit higher ⁇ i value and degree of shielding than those of material No. 24 under test of which the boron content at and near the austenite grain boundary is outside the range specified in this invention.
  • the material Nos. 2, 14, 15, 18 and 19 under test have higher initial permeability and lower coercive force. Further, in these materials under test, the deterioration of the initial permeability during application of a face pressure of 392 kPa [4 kgf/mm2] is smaller than that of the control alloys of Example 1, and it is apparent that these materials are small in the deterioration of characteristics caused by strain.
  • the material Nos. 5, 17 and 21 under test shown in Table 2 are samples in the case where the dew point of hydrogen in an atmosphere at 1,100°C for 3 hr is above -40°C.
  • the samples heat-treated under the above-described conditions exhibit a clearly low ⁇ i value, i.e., about 200,000, and a degree of shielding of about 100, i.e., lower than that of other samples of this invention.
  • the effect of this invention is properly attained by conducting heat treatment with hydrogen having a dew point of -40°C or below specified in JIS.
  • the effect of this invention can be attained also by heat treatment under high degree of vacuum. e.g., at 1 ⁇ 10 ⁇ 5 Torr.
  • Example 4 of this invention described in the above-described Example 1 and control alloy No. 23 shown in Table 3, samples were prepared under the same conditions as those of Example 2, heat-treated under magnetic annealing conditions shown in Table 4 and subjected to measurement of the magnetic properties and degree of shielding in the same manner as that of Example 2. The results are shown in Table 4.
  • alloy No. 4 of this invention substantially the same level or slightly higher level of magnetic properties after magnetic annealing can be attained at 1000°C for 1 hr. That is, it is apparent that this invention enables the magnetic annealing temperature necessary for attaining the same properties as those of the control alloy to be lowered by about 100°C.
  • the process for manufacturing a magnetic material is not limited to one described in the above Examples.
  • the material may be melted to prepare an ingot, cast into a thin cast plate, descaled as cast or after hot working, cold rolled and annealed.
  • a series of procedures of cold working, annealing for recrystallization (e.g., at 800°C or above) and cold working may be repeated instead of single cold working.
  • this invention enables the magnetic properties of the nickel-iron base magnetic alloy having high permeability to be properly improved, a high permeability magnetic alloy having magnetic characteristics, particularly permeability in a direct current and low frequency region much superior to those of the conventional PC permalloy to be provided, the alloy to be widely applied for various ceramic shielding materials, magnetic head cases where better shielding properties than those of the conventional material are required, cores and further materials for use in nonlinear applications such as magnetic amplifiers and pulse transformer, the magnetic annealing temperature necessary for attaining properties on the same level as that of the conventional material to be about 100°C lower than the conventional material, the deterioration of properties caused by strain to be small, necessary magnetic properties to be exhibited even when the alloy is formed into a structural part, such as shielding room, and the demand in electronic industry in recent years to be properly met.

Claims (4)

  1. Magnetische Nickel-Eisen-Legierung mit hoher Permeabilität, umfassend 77,5 bis 79,5 Gew.-% Nickel, 3,8 bis 4,6 Gew.-% Molybdän, 1,8 bis 2,5 Gew.-% Kupfer, 0,1 bis 1,10 Gew.-% Mangan, 0,010 Gew.-% oder weniger Phosphor, 0,0020 Gew.-% oder weniger Schwefel, 0,0030 Gew.-% oder weniger Sauerstoff, 0,0010 Gew.-% oder weniger Stickstoff, gegebenenfalls ein kleiner Anteil bis zu 0,0017 Gew.-% Calcium, und 0,020 Gew.-% oder weniger Kohlenstoff und weiterhin Bor in einer Menge innerhalb des durch die folgende Formel wiedergegebenen Bereichs: 0.0005 Gew.-%≦[B] - 10.8 14 [N] ≦ 0.0070 Gew.-%
    Figure imgb0021
     wobei die Balance, abgesehen von Verunreinigungen, aus Eisen, dem Gehalt an Nickel, Molybdän, Kupfer, Mangan und Eisen jeweils im Bereich entsprechend der folgenden Formel besteht: 3.3 ≦ 2.02 × [Ni] - 11.13 × [Mo] - 1.25 × [Cu] - 5.03 × [Mn] 2.13 × [Fe] ≦ 3.8
    Figure imgb0022
  2. Magnetische Nickel-Eisen-Legierung mit hoher Permeabilität nach Anspruch 1, umfassend 77,80 bis 79,31 Gew.-% Nickel, 3,8 bis 4,5 Gew.-% Molybdän, 2,25 bis 2,46 Gew.-% Kupfer, 0,51 bis 0,65 Gew.-% Mangan, 0,006 Gew.-% oder weniger Phosphor, 0,0016 Gew.-% oder weniger Schwefel, 0,0020 Gew.-% oder weniger Sauerstoff, 0,0006 Gew.-% oder weniger Stickstoff, 0,0016 bis 0,0017 Gew.-% Calcium, und 0,0065 Gew.-% oder weniger Kohlenstoff und weiterhin Bor in einer Menge innerhalb des Bereichs entsprechend der folgenden Formel: 0.0006 Gew.-%≦[B] - 10.8 14 [N] ≦ 0.0042 Gew.-%
    Figure imgb0023
     wobei die Balance, abgesehen von Verunreinigungen, aus Eisen, dem Gehalt an Nickel, Molybdän, Kupfer, Mangan und Eisen jeweils im Bereich entsprechend der folgenden Formel besteht: 3.3 ≦ 2.02 × [Ni] - 11.13 × [Mo] - 1.25 × [Cu] - 5.03 × [Mn] 2.13 × [Fe] ≦ 3.7
    Figure imgb0024
  3. Magnetische Nickel-Eisen-Legierung mit hoher Permeabilität nach Anspruch 1 oder 2 mit einem Borgehalt von 10 bis 50 atm% bei oder nahe der Austenitkorngrenze nach Magnetfeldglühen.
  4. Magnetische Nickel-Eisen-Legierung mit hoher Permeabilität nach Anspruch 1 oder 2 mit einem Borgehalt von etwa 11 bis 35 atm% bei oder nahe der Austenitkorngrenze nach Magnetfeldglühen.
EP90901881A 1989-01-20 1990-01-20 Magnetische nickel-eisen legierung mit hoher permeabilität Expired - Lifetime EP0407608B1 (de)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP11575/89 1989-01-20
JP1157589 1989-01-20
JP256383/89 1989-09-30
JP1256383A JPH0653903B2 (ja) 1989-01-20 1989-09-30 Ｎｉ―Ｆｅ系高透磁率磁性合金
PCT/JP1990/000067 WO1990008201A1 (fr) 1989-01-20 1990-01-20 Alliage magnetique a base de nickel et de fer a permeabilite elevee

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EP0407608A1 EP0407608A1 (de) 1991-01-16
EP0407608A4 EP0407608A4 (en) 1991-03-13
EP0407608B1 true EP0407608B1 (de) 1994-06-01

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Publication number Priority date Publication date Assignee Title
JP4240823B2 (ja) 2000-09-29 2009-03-18 日本冶金工業株式会社 Ｆｅ−Ｎｉ系パーマロイ合金の製造方法
CN101611160B (zh) 2007-02-13 2011-06-29 日立金属株式会社 磁屏蔽材料、磁屏蔽部件和磁屏蔽室

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2146755C3 (de) * 1971-09-18 1980-11-13 Fried. Krupp Gmbh, 4300 Essen Verwendung einer Legierung auf Eisen-Nickel-Basis zur Herstellung weichmagnetischer Gegenstände
JPS62227054A (ja) * 1986-03-28 1987-10-06 Sumitomo Special Metals Co Ltd 加工性のすぐれた高透磁率磁性合金
JPS62227053A (ja) * 1986-03-28 1987-10-06 Sumitomo Special Metals Co Ltd 加工性のすぐれた高透磁率磁性合金
JPH01176050A (ja) * 1987-12-29 1989-07-12 Nippon Steel Corp 表面性状に優れたＦｅ−Ｎｉ系磁性合金
JPH0250931A (ja) * 1988-05-13 1990-02-20 Nkk Corp 強磁性Ｎｉ―Ｆｅ系合金、および、前記合金の優れた表面性状を有するスラブまたは熱間圧延鋼帯を製造するための方法

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DE69009317D1 (de) 1994-07-07
EP0407608A4 (en) 1991-03-13
DE69009317T2 (de) 1995-02-09
WO1990008201A1 (fr) 1990-07-26
EP0407608A1 (de) 1991-01-16

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