EP0240600B1

EP0240600B1 - Glassy metal alloys with perminvar characteristics

Info

Publication number: EP0240600B1
Application number: EP19860115434
Authority: EP
Inventors: Ryusuke C/O Allied Corporation Hasegawa
Original assignee: AlliedSignal Inc
Current assignee: Honeywell International Inc
Priority date: 1986-01-08
Filing date: 1986-11-07
Publication date: 1992-05-13
Also published as: JPH08188858A; JP2552274B2; JPS62170446A; CA1317484C; EP0240600A1; DE3685326D1; JP2907271B2

Description

This invention relates to glassy metal alloys with Perminvar characteristics that is constant permeabilities at low magnetic field excitations and constricted hysteresis loops. More particularly, this invention provides glassy metal alloys with highly non-linear magnetic properties at low magnetic excitation levels.
The magnetic response, namely magnetic induction caused by magnetic excitation, of a typical ferromagnet, is non-linear characterized by a hysteresis loop. This loop usually does not allow a relatively constant permeability near the zero-excitation point. To realize such a feature, so-called Perminvar alloys were developed [see, for example, R. M. Bozorth, Ferromagnetism (Van Nostrand, Co., Inc., New York, 1951) p. 166-180]. These alloys are usually based on crystalline iron-cobalt-nickel system. Typical compositions (weight percent) include 20%Fe-60%Co-20%Ni (20-60 Perminvar) and 30%Fe-25%Co-45%Ni (45-45 Perminvar). Improvements of the crystalline Perminvar alloys have been made. Of significance is the addition of molybdenum, as exemplified by the synthesis of 7.5-45-25 Mo-Perminvar (7.5%Mo-45%Ni-25%Co-22.5%Fe). This material, when furnace cooled from 1110°C, exhibited a dc coercivity (H_c) of 40 A/m (=0.5 Oe), initial permeability ( µ_o) of 100 and the remanence (B_r) of 0.75 T.
In the advent of modern electronics technology, it becomes necessary to further improve the Perminvar-like properties. For example, further reduction H_c and increase of µo would be desirable when an efficient transformer requiring low field modulations is needed. Furthermore, the usual non-linear characteristic of the conventional Perminvar alloys cannot be utilized without a large level of excitation of well above 80 A/m (=1 Oe). Also desirable in many applications are low ac magnetic losses. One approach to attain these excellent soft magnetic properties is to reduce the materials' magnetostriction values as low as possible.
Saturation magnetostriction λ_s is related to the fractional change in length Δℓ/ℓ that occurs in a magnetic material on going from the demagnetized to the saturated, ferromagnetic state. The value of magnetostriction, a dimensionless quantity, is often given in units of microstrains (i.e., a microstrain is a fractional change in length of one part per million).
Ferromagnetic alloys of low magnetostriction are desirable for several interrelated reasons:

1. Soft magnetic properties (low coercivity, high permeability) are generally obtained when both the saturation magnetostriction λ_s and the magnetocrystalline anisotropy K approach zero. Therefore, given the same anisotropy, alloys of lower magnetostriction will show lower dc coercivities and higher permeabilities. Such alloys are suitable for various soft magnetic applications.
2. Magnetic properties of such zero magnetostrictive materials are insensitive to mechanical strains. When this is the case, there is little need for stress-relief annealing after winding, punching or other physical handling needed to form a device from such material. In contrast, magnetic properties of stress-sensitive materials, such as the crystalline alloys, are seriously degraded by such cold working and such materials must be carefully annealed.
3. The low dc coercivity of zero magnetostrictive materials carries over to ac operating conditions where again low coercivity and high permeability are realized (provided the magnetocrystalline anisotropy is not too large and the resistivity not too small). Also because energy is not lost to mechanical vibrations when the saturation maganetostriction is zero, the core loss of zero magnetostrictive materials can be quite low. Thus, zero magnetostrictive magnetic alloys (of moderate or low magnetocrystalline anisotropy) are useful where low loss and high ac permeability are required. Such applications include a variety of tape-wound and laminated core devices, such as power transformers, signal transformers, magnetic recording heads and the like.
4. Finally, electromagnetic devices containing zero magnetostrictive materials generate no acoustic noise under AC excitation. While this is the reason for the lower core loss mentioned above, it is also a desirable characteristic in itself because it eliminates the hum inherent in many electromagnetic devices.

There are three well-known crystalline alloys of zero magnetostriction (in atom percent, unless otherwise indicated):

(1) Nickel-iron alloys containing approximately 80% nickel ("80 nickel permalloys");
(2) Cobalt-iron alloys containing approximately 90% cobalt; and
(3) Iron-silicon alloys containing approximately 6 wt. % silicon.

Also included in these categories are zero magnetostrictive alloys based on the binaries but with small additions of other elements such as molybdenum, copper or aluminum to provide specific property changes. These include, for example, 4% Mo, 79% Ni, 17% Fe (sold under the designation Moly Permalloy) for increased resistivity and permeability; permalloy plus varying amounts of copper (sold under the designation Mumetal) for magnetic softness and improved ductility; and 85 wt. % Fe, 9 wt. % Si, 6 wt. % Al (sold under the designation Sendust) for zero anisotropy.
The alloys included in category (1) are the most widely used of the three classes listed above because they combine zero magnetostriction with low anisotropy and are, therefore, extremely soft magnetically; that is they have a low coercivity, a high permeability and a low core loss. These permalloys are also relatively soft mechanically and their excellent magnetic properties, achieved by high temperature (above 1000°C) anneal, tend to be degraded by relatively mild mechanical shock.
Category (2) alloys such as those based on Co₉₀Fe₁₀ have a much higher saturation induction (B_s about 1.9 Tesla) than the permalloys. However, they also have a strong negative magnetocrystalline anisotropy, which prevents them from being good soft magnetic materials. For example, the initial permeability of Co₉₀Fe₁₀ is only about 100 to 200.
Category (3) alloys such as Fe-6 wt% Si and the related ternary alloy Sendust (mentioned above) also show higher saturation inductions (B_s about 1.8 Tesla and 1.1 Tesla, respectively) than the permalloys. However these alloys are extremely brittle and have, therefore, found limited use in powder form only. Recently both Fe-6.5 wt. % Si [IEEE Trans. MAG-16, 728 (1980)] and Sendust alloys [IEEE Trans. MAG-15, 1149 (1970)] have been made relatively ductile by rapid solidification. However, compositional dependence of the magnetostriction is very strong in these materials, making difficult precise tayloring of the alloy composition to achieve near-zero maganetostriction.
It is known that magnetocrystalline anisotropy is effectively eliminated in the glassy state. It is therefore, desirable to seek glassy metal alloys of zero magnetostriction. Such alloys might be found near the compositions listed above. Because of the presence of metalloids which tend to reduce the magnetization by dilution and electronic hybridization, however, glassy metal alloys based on the 80 nickel permalloys are either non-magnetic at room temperature or have unacceptably low saturation inductions. For example, the glassy alloy Fe₄₀Ni₄₀P₁₄B₆ (the subscripts are in atom percent) has a saturation induction of about 0.8 Tesla, while the glassy alloy Ni₄₉Fe₂₉P₁₄B₆Si₂ has a saturation induction of about 0.46 Tesla and the glassy alloy Ni₈₀P₂₀ is non-magnetic. No glassy metal alloys having a saturation magnetostriction approximately equal to zero have yet been found near the iron-rich Sendust composition. A number of near-zero magnetostrictive glassy metal alloys based on the Co-Fe crystalline alloy mentioned above in (2) have been reported in the literature. These are, for example, Co₇₂Fe₃P₁₆B₆Al₃ (AIP Conference Proceedings, No. 24, pp. 745-746 (1975)) Co_70.5Fe_4.5Si₁₅B₁₀ Vol. 14, Japanese Journal of Applied Physics, pp. 1077-1078 (1975)) Co_31.2Fe_7.8Ni_39.0B₁₄Si₈ [proceedings of 3rd International Conference on Rapidly Quenched Metals, p. 183, (1979)] and Co₇₄Fe₆B₂₀ [IEEE Trans. MAG-12, 942 (1976)]. However, none of the above-mentioned near-zero magnetostrictive materials show Perminvar-like characteristics. By polishing the surface of a low magnetostrictive glassy ribbon, a surface uniaxial anisotropy was introduced along the polishing direction which resulted in observation of Perminvar-like Kerr hysteresis loops (Applied Physics Letters, vol. 36, pp. 339-341 (1980). This is only a surface effect and is not of a bulk property of the material, limiting the use of such effect in some selected devices.
Furthermore, to realize the Perminvar properties, the crystalline materials mentioned-above have to be baked for a long time at a given temperature. Typically the heat-treatment is performed at 425°C for 24 hours. Obviously it is desirable to heat-treat the materials at a temperature as low as possible and for a duration as short as possible.
EP-A-84138 discloses glassy metal alloys of near zero magnetostriction having the formula Co_aFe_bNi_cMo_dB_eSi_f, where "a" to "f" are in atom percent, a is from 58 to 70, b is from 2 to 75, c is from 0 to 8, d is from 1 to 2, e is from 11 to 15 and f is from 9 to 14, the sum of a, b and c being from 72 to 76 and the sum of e and f being from 23 to 26. There is no description of how to obtain therefrom any alloy having Perminvar characteristics.
Clearly desirable are new magnetic materials with various Perminvar characteristics which are suited for modern electronics technology.
According to the invention there is provided a magnetic alloy that is at least 70% glassy, having the formula Co_aFe_bNi_cM_dB_eSi_f, where M is at least one of Cr, Mo, Mn and Nb, "a" - "f" are in atom percent and the sums of "a" - "f" equals 100, "a" is from 66 to 71, "b" is from 2.5 to 4.5, "c" is from 0 to 3, "d" is from 0 to 4, "e" is from 6 to 24 and "f" is from 0 to 19, with the provisos that the sum of "a", "b" and "c" is from 71 to 76 and the sum of "e" and "f" is from 25 to 27 and up to 4 atom percent of Si may be replaced by C, Al and Ge, said alloy having a value of magnetostriction between - 1x10⁻⁶ and + 1x10⁻⁶, said alloy having Perminvar characteristics of a relatively constant permeability at low magnetic excitation and a constricted hysteresis loop as a result of having been heat-treated by heating to a temperature between 50 and 110°C below the first crystallization temperature thereof for from 15 to 180 minutes and then cooling at a rate slower than about - 60°C/min.
The invention will be more fully understood and further advantages will become apparent when reference is made to the following detailed description of the invention and the accompanying drawing, which is a graph depicting the B-H characteristics of an alloy which has been annealed for fifteen minutes at the temperatures (A) 460°C, (B) 480°C and (C) 500°C.
The glassy alloy is heat-treated at a temperature T_a for a duration of time t_a, where ΔT_c-a = (T_cl-T_a) is between 50 and 110°C; and t_a is between 15 and 120 minutes, followed by cooling of the material at a rate slower than about -60°C/min. The choice of T_a and t_a should exclude the case that ΔT_c-a ∼ 50°C and t_a
15 minutes because such combination sometimes results in crystallization of the glassy alloy.
The purity of the above composition is that found in normal commercial practice. However, it would be appreciated that the metal M in the alloys may be replaced by at least one other element such as vanadium, tungsten, tantalum, titanium, zirconium and hafnium, and up to 4 atom percent of Si may be replaced by carbon, aluminum or germanium without significantly degrading the desirable magnetic properties of these alloys.

Examples of near-zero magnetostrictive glassy metal alloys for heat treatment in accordance with the invention include Co_70.5Fe_4.5B₁₅Si₁₀, Co_69.0Fe_4.1Ni_1.4Mo_1.5B₁₂Si₁₂, Co_65.7Fe_4.4Ni_2.9Mo₂B₁₁Si₁₄, Co_69.2Fe_3.8Mo₂B₈Si₁₇, Co_67.5Fe_4.5Ni_3.0B₈Si₁₇, Co_70.9Fe_4.1B₈Si₁₇, Co_69.9Fe_4.1Mn_1.0B₈Si₁₇, Co_69.0Fe_4.0Mn₂B₈Si₁₇, Co_68.0Fe_4.0Mn₃B₈Si₁₇, Co_67.1Fe_3.9Mn₄B₈Si₁₇, Co_68.0Fe_4.0Mn₂Cr₁B₈Si₁₇, Co_69.0Fe_4.0Cr₂B₈Si₁₇, Co_69.0Fe_4.0Nb₂B₈Si₁₇, Co_68.2Fe_3.8Mn₁B₁₂Si₁₅, Co_67.7Fe_3.3Mn₂B₁₂Si₁₅, Co_67.8Fe_4.2Mo₁B₁₂Si₁₅, Co_67.8Fe_4.2Cr₁B₁₂Si₁₅, Co_67.0Fe_4.0Cr₂B₁₂Si₁₅, Co_66.1Fe_3.9Cr₃B₁₂Si₁₅,Co_68.5Fe_2.5Mn₄B₁₀Si₁₅, Co_65.7Fe_4.4Ni_2.9Mo₂B₂₃C₂ and Co_68.6Fe_4.4Mo₂Ge₄B₂₁.
These alloys possess saturation induction (B_s) between 0.5 and 1 Tesla, Curie temperature between 200 and 450°C and excellent ductility. Some magnetic and thermal properties of these and some of other near-zero magnetostrictive alloys are listed in Table I.

TABLE I

Saturation induction (B_s), Curie temperature ( ϑ_f), saturation magnetostriction ( λ_s) and the first crystallization temperature (T_cl) of near-zero magnetostrictive alloys for heat treatment in accordance with the present invention.
Compositions
Co	Fe	Ni	M	B	Si
70.5	4.5	-	-	15	10
69.0	4.1	1.4	Mo=1.5	12	12
65.7	4.4	2.9	Mo=2	11	14
68.2	3.8	-	Mn=1	12	15
67.7	3.3	-	Mn=2	12	15
67.8	4.2	-	Mo=1	12	15
67.8	4.2	-	Cr=1	12	15
69.2	3.8	-	Mo=2	8	17
67.5	4.5	3.0	-	8	17
70.9	4.1	-	-	8	17
69.9	4.1	-	Mn=1	8	17
69.0	4.0	-	Mn=2	8	17
68.0	4.0	-	Mn=3	8	17
67.1	3.9	-	Mn=4	8	17
69.0	4.0	-	Cr=2	8	17
68.0	4.0	-	Mn=2,Cr-1	8	17
69.0	4.0	-	Nb=2	8	17
65.7	4.4	2.9	Mo=2	23	C=3*
65.7	4.4	2.9	Mo=2	23	2
69.5	4.1	1.4	-	6	19
68.6	4.4	-	Mo=2	21	Ge=4*
70.5	4.5	-	-	24	Ge=1*
67.0	4.0	-	Cr=2	12	15
69.2	3.8	-	Mo=2	10	15
68.1	4.0	1.4	Mo=1.5	8	17
69.0	3.0	-	Mn=3	10	15
68.5	2.5	-	Mn=4	10	15
68.8	4.2	-	Cr=2	10	15

* All Si content is replaced by the indicated element and amount.

B_s(Tesla)	ϑ f(°C)	λ s(10⁻⁶)	T_cl(°C)
0.82	422	-0.3	517
0.73	324	0	520
0.77	246	0	530
0.70	266	+0.4	558
0.71	246	+0.4	560
0.62	227	+0.4	556
0.64	234	+0.6	561
0.67	295	+0.5	515
0.73	329	+0.5	491
0.77	343	-0.4	490
0.77	331	-0.5	493
0.75	312	+0.8	502
0.74	271	+0.9	507
0.74	269	-0.8	512
0.63	261	+0.2	503
0.69	231	+0.7	511
0.62	256	+0.4	541
0.76	393	0	500
0.79	402	0	512
0.73	316	-0.1	443
0.77	365	0	570
0.99	451	-0.4	494
0.57	197	+0.4	480
0.72	245	+0.4	541
0.67	276	+0.4	512
0.79	305	+1.1	544
0.78	273	+0.4	548
0.69	261	+0.4	540

Figure 1 illustrates the B(induction)-H(applied field) hysteresis loops for a near-zero magnetostrictive Co_67.8Fe_4.2Cr₁B₁₂Si₁₅ glassy alloy heat-treated at T_a = 460°C (A), T_a = 480°C (B) and T_a = 500°C (C) for 15 minutes, followed by cooling at a rate of about -5°C/min. The constricted B-H loops of Figs 1B and 1C are characteristic of the materials with Perminvar-like properties, whereas the B-H loop of Fig. 1A corresponds to that of a typical soft ferromagnet. As evidenced in Figure 1, the choice of the heat-treatment temperature T_a is very important in obtaining the Perminvar characteristics in the glassy alloys. Table II summarizes the heat-treatment conditions for some of these alloys and some of the resultant magnetic properties.
This table teaches the importance of the quantity ΔT_c-a being between 50 and 110°C and relatively slow cooling rates after the heat-treatments at temperature T_a and for the duration t_a. It is also noted that µ_o values are higher and the H_c values are lower than those of prior art materials. For example, a properly heat-treated (T_a = 480°C; t_a = 15 min.) Co_67.8Fe_4.2Cr₁B₁₂Si₁₅ glassy alloy exhibits µ_o = 50,000 and H_c = 0.2 A/m whereas one of the improved prior art alloy, namely 7.5-45-25 Mo-Perminvar, gives µ_o = 100 and H_c = 40 A/m when furnace cooled from 1100°C and gives µ_o = 3,500 when quenched from 600°C.
In many magnetic applications, lower magnetostriction is desirable. For some applications, however, it may be desirable or acceptable to use materials with a small positive or negative magnetostriction. Such near-zero magnetostrictive glassy metal alloys are obtained for "a", "b", "c" in the ranges of 66 to 71, 2.5 to 4.5 and 0 to 3 atom percent respectively, with the proviso that the sum of "a", "b", and "c" ranges between 72 and 76 atom percent. The absolute value of saturation magnetostriction | λ_s| of these glassy alloys is less than about 1x10⁻⁶ (i.e. the saturation magnetostriction ranges from -1x10⁻⁶ to +1x10⁻⁶ or from -1 to +1 microstrains).
The glassy alloys of the invention are conveniently prepared by techniques readily available elsewhere; see e.g. US Patent No. 3,845,805 and No. 3,856,513. In general, the glassy alloys, in the form of continuous ribbon or wire, are rapidly quenched from a melt of the desired composition at a rate of at least about 10⁵ K/sec.
A metalloid content of boron and silicon in the range of 25 to 27 atom percent of the total alloy composition is sufficient for glass formation with boron ranging from 6 to 24 atom percent. It is prefered, however, that the content of metal M, i.e. the quantity "d" does not exceed very much 2 atom percent except when M=Mn to maintain a reasonably high Curie temperature (≧ 200°C).
In addition to the highly non-linear nature of the glassy Perminvar alloys of the present invention, these alloys exhibit high permeabilities and low core loss at high frequencies. Some examples of these features are given in Table III.

EXAMPLES

1. Sample Preparation

The glassy alloys listed in Tables I-III were rapidly quenched (about 10⁶ K/sec) from the melt following the techniques taught by Chen and Polk in U.S. Patent 3,856,513. The resulting ribbons, typically 25 to 30 µm thick and 0.5 to 2.5 cm wide, were determined to be free of significant crystallinity by X-ray diffractometry (using CuK radiation) and scanning calorimetry. Ribbons of the glassy metal alloys were strong, shiny, hard and ductile.

2. Magnetic Measurements

Continuous ribbons of the glassy metal alloys prepared in accordance with the procedure described in Example I were wound onto bobbins (3.8 cm O.D.) to form closed-magnetic-path toroidal samples. Each sample contained from 1 to 3 g of ribbon. Insulated primary and secondary windings (numbering at least 10 each) were applied to the toroids. These samples were used to obtain hysteresis loops (coercivity and remanence) and initial permeability with a commercial curve tracer and core loss (IEEE Standard 106-1972).
The saturation magnetization, M_s, of each sample, was measured with a commercial vibrating sample magnetometer (Princeton Applied Research). In this case, the ribbon was cut into several small squares (approximately 2 mm x 2 mm). These were randomly oriented about their normal direction, their plane being parallel to the applied field (0 to 720 kA/m. The saturation induction B_s (=4πM_sD) was then calculated by using the measured mass density D.
The ferromagnetic Curie temperature ( ϑ_f) was measured by inductance method and also monitored by differential scanning calorimetry, which was used primarily to determine the crystallization temperatures.
Magnetostriction measurements employed metallic strain gauges (BLH Electronics), which were bonded (Eastman - 910 Cement) between two short lengths of ribbon. The ribbon axis and gauge axis were parallel. The magnetostriction was determined as a function of applied field from the longitudinal strain in the parallel ( Δℓ/ ℓ) and perpendicular ( Δ ℓ/ℓ)
in-plain fields, according to the formula

Claims

A magnetic alloy that is at least 70% glassy, having the formula Co_aFe_bNi_cM_dB_eSi_f, where M is at least one of Cr, Mo,Mn and Nb, "a" - "f" are in atom percent and the sums of "a" - "f" equals 100, "a" is from 66 to 71, "b" is from 2.5 to 4.5, "c" is from 0 to 3, "d" is from 0 to 4, "e" is from 6 to 24 and "f" is from 0 to 19, with the provisos that the sum of "a", "b" and "c" is from 71 to 76 and the sum of "e" and "f" is from 25 to 27 and up to 4 atom percent of Si may be replaced by C, Al or Ge, said alloy having a value of magnetostriction between - 1x10⁻⁶ and + 1x10⁻⁶, said alloy having Perminvar characteristics of a relatively constant permeability at low magnetic excitation and a constricted hysteresis loop as a result of having been heat-treated by heating to a temperature between 50 and 110^oC below the first crystallization temperature thereof for from 15 to 180 minutes and then cooling at a rate slower than about - 60^oC/min.
A magnetic alloy according to claim 1 having the formula Co_70.5Fe_4.5B₁₅Si₁₀.
A magnetic alloy according to claim 1 having the formula Co_65.7Fe_4.4Ni_2.9Mo₂B₁₁Si₁₄.
A magnetic alloy according to claim 1 having the formula Co_68.2Fe_3.8Mn₁B₁₂Si₁₅.
A magnetic alloy according to claim 1 having the formula Co_67.7Fe_3.3Mn₂B₁₂Si₁₅.
A magnetic alloy according to claim 1 having the formula Co_67.8Fe_4.2Mo₁B₁₂Si₁₅.
A magnetic alloy according to claim 1 having a formula selected from
Co_67.8Fe_4.2Cr₁B₁₂Si₁₅, Co_69.2Fe_3.8Mo₂B₈Si₁₇, Co_67.5Fe_4.5Ni_3.0B₈Si₁₇, Co_70.9Fe_4.1B₈Si₁₇, Co_69.9Fe_4.1Mn_1.0B₈Si₁₇, Co_69.0Fe_4.0Mn₂B₈Si₁₇, Co_68.0Fe_4.0Mn₃B₈Si₁₇, Co_67.1Fe_3.9Mn₄B₈Si₁₇, Co_69.0Fe_4.0Cr₂B₈Si₁₇, Co_68.0Fe_4.0Mn₂Cr₁B₈Si₁₇, Co_69.0Fe_4.0Nb₂B₈Si₁₇, Co_67.0Fe_4.0Cr₂B₁₂Si₁₅,