EP0121046B1 - Alliage amorphe par une tête magnétique et tête magnétique avec un alliage amorphe - Google Patents

Alliage amorphe par une tête magnétique et tête magnétique avec un alliage amorphe Download PDF

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Publication number
EP0121046B1
EP0121046B1 EP19840100955 EP84100955A EP0121046B1 EP 0121046 B1 EP0121046 B1 EP 0121046B1 EP 19840100955 EP19840100955 EP 19840100955 EP 84100955 A EP84100955 A EP 84100955A EP 0121046 B1 EP0121046 B1 EP 0121046B1
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Prior art keywords
amorphous alloy
magnetic head
alloy
magnetic
inequality
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EP19840100955
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German (de)
English (en)
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EP0121046A2 (fr
EP0121046A3 (en
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Hiroshi Tateishi
Masakatsu Haga
Susumu Hashimoto
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Toshiba Corp
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Toshiba Corp
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Priority claimed from JP58053769A external-priority patent/JPS59179748A/ja
Priority claimed from JP58136608A external-priority patent/JPS6044383B2/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/04—Amorphous alloys with nickel or cobalt as the major constituent
    • 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
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15316—Amorphous metallic alloys, e.g. glassy metals based on Co

Definitions

  • the present invention relates to an amorphous alloy which is used as a core material for a magnetic head, and a magnetic head with an amorphous alloy.
  • a highly magnetic permeable material having a crystalline structure is employed, such as an Fe-Ni alloy (Permalloy) or an Fe-Si-Al alloy (Sendust).
  • Fe-Ni alloy Permalloy
  • Fe-Si-Al alloy Fe-Si-Al alloy
  • the Fe-Ni alloy has a disadvantage, in that its wear resistance is low; and, although the Fe-Si-AI alloy has good wear resistance, it also has disadvantages, in that its mechanical strength, brittleness and plastic processing capacity is low.
  • the amorphous alloy having no crystalline structure such as a Co-Fe-Ni-Si-B alloy, has recently been identified as an ideal material for a magnetic head.
  • Such amorphous alloys have excellent magnetic properties, such as high saturation magnetization and low magnetostriction, along with high mechanical strength, good wear resistance and good processing capacity.
  • the magnetic head used for a VTR (video tape recorder) must be stably and rigidly. Therefore, especially, the core halves of the magnetic head of a VTR are normally secured each other with a glass adhesive to form the gap.
  • the glass bonding process involved requires heat treatment at a temperature higher than 400°C, and a gradual cooling after heat treatment.
  • the amorphous alloys all have their respective crystallization temperatures; and the magnetic properties and, particularly, the effective magnetic permeability of the amorphous alloy are deteriorated by heat treatment at a temperature in the vicinity of the crystallization temperature.
  • the conventional low magnetostriction amorphous alloys contain at least two or more of the magnetic elements comprised of Co, Fe and Ni.
  • the conventional amorphous alloys have disadvantages, in that the practicability of using them for the magnetic head of a VTR is low.
  • an amorphous alloy whose magnetic properties do not deteriorate after glass bonding; i.e., for an amorphous alloy which has a crystallization temperature higher than the- temperature necessary for a glass bonding heat treatment (i.e., higher than 500°C), whose magnetic properties do not deteriorate, even with the gradual cooling which occurs after heat treatment. If only one of the magnetic elements is contained in the amorphous alloy, the deterioration, after gradual cooling, of the effective magnetic permeability of an amorphous alloy having this composition can be prevented.
  • such an amorphous alloy has certain disadvantages, in that the requirements for high saturation magnetization and low magnetostriction cannot be satisfied.
  • a magnetic head with an amorphous alloy bonded by a glass adhesive is not yet provided, which magnetic head has high saturation magnetization and low magnetostriction and maintains a high level of effective magnetic permeability.
  • EP-A-21101 discloses an amorphous soft magnetic alloy with various constituents and indispensibly Mn to achieve low saturation magnetostriction of :-5 5.10- c .
  • a primary object of the present invention is to provide an amorphous alloy for a magnetic head, which alloy has excellent magnetic properties, such as high saturation magnetization and low magnetostriction.
  • Another object of the present invention is to provide an amorphous alloy for a magnetic head, which alloy has a crystallization temperature higher than 500°C and undergoes no deterioration of its magnetic properties, such as its effective magnetic permeability, even in a heat treatment combined with a gradual cooling.
  • Still another object of the present invention is to provide a magnetic head which exhibits excellent magnetic properties, without lowering its effective magnetic permeability, even if a core composed of an amorphous alloy having high saturation magnetization and low magnetostriction is subjected to a glass bonding heat treatment.
  • an amorphous alloy for a magnetic head which alloy has a composition represented by the following formula: where M represents Ni or Re. T, X, Y and Z respectively represent the atomic density of elements M (Ni or Re), Hf, B and Si, and satisfy the following inequalities:
  • An amorphous alloy for a magnetic head comprises a substance represented by the following formula: where M represents either element Ni or Re. T, X, Y or Z represent the atomic density of the element M (Ni or Re), Hf, B or Si in the amorphous alloy. In this case, the composition of the amorphous alloy is so determined that the T, X, Y and Z factors are contained within the ranges of contents represented by the following inequalities:
  • An amorphous alloy according to the present invention mainly comprises a cobalt (Co).
  • a cobalt Co
  • an amorphous alloy having a saturation magnetization higher than 0,8 T (8 kGauss) and low magnetostriction (A,) ( I ⁇ s ⁇ 10 -6 ) can be readily obtained.
  • Ni or Re is contained in the amorphous alloy because the nickel (Ni) or rhenium (Re) serves to raise the crystallization temperature of the alloy and lower the magnetostriction.
  • the atomic density T of the Ni or Re is so set as to satisfy the above formula (1); since, if the atomic density T is lower than 0.2 and higher than 14, the adding effect of the Ni or Re cannot be readily obtained.
  • the atomic density T of the Ni is preferable to set within a range of from 0.75 to 14, when the Ni is contained in the amorphous alloy.
  • the Ni has the effect of enhancing the crystallization temperature and also increasing the magnetic permeability of the amorphous alloy. In this case, the effect of enhancing the magnetic permeability can be preferably obtained within the above range of atomic density.
  • the atomic density T of the Re is set within a range of from 0.2 to 6, when the Re is contained in the amorphous alloy.
  • the Re has the effect of lowering the saturation magnetostriction constant of the alloy, with the addition of small amounts. When this effect is substantial, the saturation magnetostriction constant might become a negative value, with the addition of the Re.
  • the atomic density T of the Re is set at a level higher than 0.2; since, if the Re is lower than 0.2, the effect whereby the saturation magnetostriction constant is lowered by the addition of the Re is lessened.
  • the atomic density T of the Re is set lower than 6; since, if the Re is more than 6, the saturation magnetization of the alloy, by the addition of the Re, is reduced.
  • the Re has the effect of raising the saturation magnetization level of the alloy.
  • the figure shows the variation in the saturation magnetization level which occurs in cases wherein the atomic density T of the Re is altered in the alloy CO 78.5 - T Re T Hf 11.5 B 10.0 , i.e., the saturation magnetization effect which occurs in cases where the Co is substituted for the Re.
  • the saturation magnetization level of the alloy can be raised by setting the atomic density T of the Re within a range of from 0.2 to 1.5. Therefore, an amorphous alloy which has a high crystallization temperature, a low saturation magnetostrictive constant and a high saturation magnetization level may be provided, by setting the atomic density T of the Re within a range of from 0.2 to 1.5.
  • the hafnium (Hf) is contained in the amorphous alloy according to the present invention because the Hf has the effect of raising the crystallization temperature of the alloy.
  • the atomic density X of Hf is so set as to satisfy the above formula (2); since, if the X is lower than 6, a crystallization temperature higher than 500°C cannot be obtained and, similarly, if the X is higher than 15, a crystallization temperature higher than 500°C cannot be obtained and it will be difficult to raise the saturation magnetization level of the alloy above 0,8 T (8 kGauss).
  • the boron (B) is contained in the amorphous alloy of the invention because the B has the effect of aiding in the formation of the amorphous alloy. and improving the physical properties of the alloy.
  • the atomic density Y of the B is so set as to satisfy the above formula (3); since, if the Y is lower than 3, the effect of aiding in the formation of the amorphous alloy with the B is lessened and, if the Y is higher than 14, the rust resistance of the alloy deteriorates and brittleness is produced. It is preferable to set the atomic density Y of the B lower than 8; since, if the atomic density Y of the B is less than 8, the production of the amorphous alloy is facilitated and its wear resistance can be improved.
  • the X and Y at such a level as to satisfy the following inequality (7), when the alloy contains the Re. If the X/(X+Y) factor is lower than 0.5, the effect whereby the magnitude of the saturation magnetostriction is reduced by the addition of the Re cannot be obtained. If the X/(X+Y) factor is higher than 5/6, the formation of an amorphous alloy becomes difficult, and an amorphous alloy having high saturation magnetization cannot be obtained.
  • the addition of the silicon (Si) is effective in aiding the formation of the amorphous alloy.
  • the atomic density Z of the Si is so set as to satisfy the above formula (4).
  • the formation of the amorphous alloy can be performed by including another element, such as B, even if the Si is not contained in the alloy.
  • the atomic density Z of the Si is so set as to be lower than 11; since, if it is higher than 11, the effect of forming the amorphous alloy by the addition of the Si is lessened.
  • said amorphous alloy should not contain the Si.
  • the atomic density Z of the Si is set within a range of from 0 to 0.01, an alloy can be obtained which has magnetic properties substantially similar to an alloy having no Si. Therefore, it is preferable to set the atomic density Z of the Si within a range of from 0 to 0.01.
  • the atomic densities X, Y, Z of the Hf, B and Si are so set as to satisfy the above formulae (5), (6). If the total addition amount of the B and Si is lower than 3 at atomic density Y+Z, the formation of the amorphous alloy is rendered difficult; and, if higher than 13, an alloy having a magnetic permeability higher than 5,000 (in 1 kHz) cannot be obtained.
  • the crystallization temperature of the alloy is decreased to a level tower- than 500°C; and, when higher than 25, the saturation magnetic flux density is decreased to a level lower than 0,7 T (7 kGauss), with the result that an actual problem occurs in the material used for the magnetic head.
  • the amorphous alloy which contains the composition described above is produced by the steps of preparing powders of Co, Ni (or Re), Hf, B and Si (as required) at a predetermined ratio, melting them, and forming the molten metals into an amorphous alloy by e.g., a liquid quenching method or a sputtering method.
  • the amorphous alloy may be heat treated, as required.
  • a magnetic head can be produced from the core material which is obtained by machining the amorphous alloy in a predetermined shape.
  • a rotary magnetic head device for a VTR can be constructed by mounting the magnetic head on a rotor; or, a rotary magnetic head device might also be constructed by a thin film forming technique, by directly forming a core at a rotor and further forming a coil pattern.
  • the amorphous alloy according to the present invention has a crystallization temperature level higher than 500°C and does sustain no decrease in its effective magnetic permeability, even if a heat treatment process with the gradual cooling needed for glass bonding is carried out to make a head tip. Therefore, a magnetic head which has excellent electromagnetic conversion properties, and magnetic properties such as a high saturation magnetization level, a low magnetostriction level, high effective magnetic permeability, high mechanical strength and high wear resistance can be obtained by fabricating the head from the amorphous alloy of the present invention.
  • Examples 1 to 4 and Comparative Examples 1 to 6 of the Ni-series amorphous alloy are listed.
  • Examples 5 to 7 and Comparative Examples 7 to 11 of the Re-series amorphous alloy are listed.
  • Amorphous alloys of the compositions listed in Tables 1 and 2 were respectively prepared by a liquid quenching method. More particularly, thin strip specimens of an amorphous alloy, which were 30 pm thick and 12 mm wide, were produced by injecting the molten alloys of the above compositions on the surface of a sole roll rotating at a high rate of speed in an argon gas atmosphere through argon gas under pressure (0,098 ⁇ 0,98 bar (0.1-1.0 kg/cm 2 )) from the nozzle of a quartz tube; and by then quenching the alloys.
  • Comparative Example 1 contained no Hf; the specimens in Comparative Example 2 contained B and Si, so that the total amount Y+Z of the atomic densities of the B and Si exceeded 13; Comparative Example 3 contained Hf, B and Si, so that the total amount X+Y+Z of the atomic densities exceeded 25; Comparative Example 4 contained Hf but no Ni; and Comparative Example 5 contained Hf, so that the atomic density X of the Hf exceeded 15.
  • Comparative Example 6 employed an Mn-Zn ferrite of the head material which is currently used in domestic VTRs. General data, excepting the crystallization temperatures, was listed in Table 1.
  • Comparative Example 7 contained less than half the ratio X/(X+Y) of the Hf to the sum of the Hf and the B, Comparative Example 8 contained Hf in such an amount that the atomic density Y of the Hf exceeded 15, Comparative Example 9 contained no Re, Comparative Example 10 contained Nb (instead of the Re), and Comparative Example 11 contained no Re and no Hf.
  • the thin strip specimens were punched in a ring shape, having a 10 mm outer diameter and an 8 mm inner diameter, and ten sheets of the specimens were laminated via interlayer insulators, i.e. sputtered films of soda glass having a softening point of 380°C. Then, after the laminate was heat treated at 500°C to 530°C for 30 min., it was gradually cooled at a rate of 3°C per minute, and laminated cores were obtained.
  • the laminated cores of the amorphous alloy were respectively wound with 30 turns of primary and secondary coils, the inductances were measured by an impedance meter, and the effective magnetic permeability u' levels were obtained by calculation.
  • the thin amorphous alloy strip specimens were respectively cut to form magnetic head cores for a VTR, and the wear resistances of the heads were measured. Wear resistance was evaluated by observing the tape sliding surface of the magnetic head before and after a VTR cassette tape coated with y-Fe 2 0 3 was fed on the magnetic head for 500 hours, from the side surface by an optical microscope; and thereby obtaining wear amounts converted to that per 100 hours.
  • compositions of the specimens and the measured values of magnetic properties were listed in Tables 1 and 2.
  • the crystallization temperatures of the amorphous alloys of Examples 1 to 4 were confirmed to be higher, by approx. 300°C, than those of the amorphous alloy containing no Hf.
  • the magnetic properties and, particularly, the effective magnetic permeabilities 1-1' (5 MHz) of the specimens heat treated with gradual cooling of Examples 1 to 4 were not deteriorated, as compared to those of the Comparative Examples 1 to 5.
  • Comparative Example 7 the saturation magnetostriction constant is of a large value, since ratio X/(X+Y) is less than 0.5; and Comparative Example 8 has an extremely small saturation magnetization value, since the atomic density of the Hf exceeds 15. Further, Comparative Examples 9 and 10 have remarkably large saturation magnetostriction constants, since Comparative Example 9 contained no Re and Comparative Example 10 contained Nb (instead of the Re).
  • the amorphous alloy of Comparative Example 11 was considered to exhibit excellent magnetic properties as a material for a conventional magnetic head; since the crystallization temperature is low, e.g., 380°C, it is crystallized by glass bonding at 500°C, and the value of the effective magnetic permeability after bonding becomes extremely small.
  • the amorphous alloys of Examples 5 to 7 all have high crystallization temperatures (higher than 500°C) and high saturation magnetization levels (higher than 8 kGauss); sustain no deterioration in their effective magnetic permeabilities, even from the gradual cooling which occurs after glass bonding; and exhibit saturation magnetostriction constants of small value, such as on the order of 10- 7 , as an absolute value.
  • a magnetic head using an amorphous alloy may be obtained, the magnetic properties of which are not influenced by glass bonding.
  • the Hf used in the amorphous alloys for the magnetic heads of Examples 5 to 7 were 99.8% pure; and, that, though such alloys are approx. 0.02% Zr in content, an impurity such as this (Zr) does not affect the advantages of the present invention. Even where Hf of relatively low purity (such as one which is 95% and is approx. 3% Zr in content) is employed, it has been confirmed that the advantages of the amorphous alloy according to the present invention can still be obtained.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
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Claims (12)

1. Alliage amorphe pour tête magnétique, caractérisé en ce qu'il répond à une formule de composition représentée de la façon suivante:
Figure imgb0069
dans laquelle M représente Ni ou Re, et T, X, Y et Z représentent respectivement les densités atomiques des éléments M (Ni ou Re), Hf, B et Si, et obéissent aux inégalités suivantes des formules (1) à (6):
Figure imgb0070
Figure imgb0071
Figure imgb0072
Figure imgb0073
Figure imgb0074
Figure imgb0075
2. Alliage amorphe pour tête magnétique selon la revendication 1, caractérisé en ce que le facteur M est Ni, et le facteur T obéit à l'inégalité de la formule (8) suivante:
Figure imgb0076
3. Alliage amorphe pour tête magnétique selon la revendication 1, caractérisé en ce que le facteur M est Re, le facteur T obéit à l'inégalité de la formule (9), et les facteurs X et Y obéissent à l'inégalité de la formule (7), de la façon suivante:
Figure imgb0077
Figure imgb0078
4. Alliage amorphe pour tête magnétique selon la revendication 3, caractérisé en ce que le facteur T obéit à l'inégalité de la formule (10) suivante:
Figure imgb0079
5. Alliage amorphe pour tête magnétique selon la revendication 2 ou la revendication 4, caractérisé en ce que le facteur Y obéit à l'inégalité de la formule (11) suivante:
Figure imgb0080
6. Alliage amorphe pour tête magnétique selon la revendication 2 ou la revendication 4, caractérisé en ce que le facteur Z obéit à l'inégalité de la formule (12) suivante:
Figure imgb0081
7. Tête magnétique dont le noyau est constitué par un alliage amorphe, caractérisée en ce que le noyau est constitué par un alliage amorphe répondant à une formule de composition représentée de la façon suivante:
Figure imgb0082
dans laquelle M représente Ni ou Re, et T, X, Y et Z représentent respectivement les densités atomiques des éléments M (Ni ou Re), Hf, B et Si, et obéissent aux inégalités suivantes des formules (1) à (6):
Figure imgb0083
Figure imgb0084
Figure imgb0085
Figure imgb0086
Figure imgb0087
Figure imgb0088
8. Tête magnétique à alliage amorphe selon la revendication 7, caractérisée en ce que le facteur M est Ni, et le facteur T obéit à l'inégalité de la formule (8) suivante:
Figure imgb0089
9. Tête magnétique à alliage amorphe selon la revendication 7, caractérisé en ce que le facteur M est Re, le facteur T obéit à l'inégalité de la formule (9) et les facteurs X et Y obéissent à l'inégalité de la formule (7), de la façon suivante:
Figure imgb0090
Figure imgb0091
10. Tête magnétique à alliage amorphe selon la revendication 9, caractérisée en ce que le facteur T obéit à l'inégalité de la formule (10) suivante:
Figure imgb0092
11. Tête magnétique à alliage amorphe selon la revendication 8 ou la revendication 10, caractérisée en ce que le facteur Y obéit à l'inégalité de la formule (11) suivante:
Figure imgb0093
12. Tête magnétique à alliage amorphe selon la revendication 8 ou la revendication 10, caractérisée en ce que le facteur Z obéit à l'inégalité de la formule (12) suivante:
Figure imgb0094
EP19840100955 1983-03-31 1984-01-31 Alliage amorphe par une tête magnétique et tête magnétique avec un alliage amorphe Expired EP0121046B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP53769/83 1983-03-31
JP58053769A JPS59179748A (ja) 1983-03-31 1983-03-31 磁気ヘツド用非晶質合金
JP58136608A JPS6044383B2 (ja) 1983-07-26 1983-07-26 磁気ヘツド用非晶質合金
JP136608/83 1983-07-26

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EP0121046A2 EP0121046A2 (fr) 1984-10-10
EP0121046A3 EP0121046A3 (en) 1986-11-26
EP0121046B1 true EP0121046B1 (fr) 1990-04-18

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Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2924280A1 (de) * 1979-06-15 1981-01-08 Vacuumschmelze Gmbh Amorphe weichmagnetische legierung
WO1981000861A1 (fr) * 1979-09-21 1981-04-02 Hitachi Metals Ltd Alliages amorphes
US4578728A (en) * 1981-12-09 1986-03-25 Matsushita Electric Industrial Co., Ltd. Magnetic head

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EP0121046A2 (fr) 1984-10-10
EP0121046A3 (en) 1986-11-26

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