FIELD OF INVENTION The present invention relates to metallic glass alloys for use in electronic article surveillance systems.

BACKGROUND OF INVENTION Metallic glass alloys (amorphous metal alloys or metallic glasses) have been disclosed in U. S. Patent No. 3,856,513, issued Dec. 24,1974 to H. S. Chen et al. (the"'513"Patent) These alloys include compositions having the formula MaYbZ, where M is a metal selected from the group consisting of iron, nickel, cobalt, vanadium and chromium; Y is an element selected from the group consisting of phosphorus, boron and carbon ; Z is an element selected from the group consisting of aluminum, silicon, tin, germanium, indium, antimony and beryllium;"a"ranges from about 60 to 90 atom percent;"b"ranges from about 10 to 30 atom percent; and"c"ranges from about 0.1 to 15 atom percent. Also disclosed are metallic glass wires having the formula TiXj, where T is at least one transition metal and X is an element selected from the group consisting of phosphorus, boron, carbon, aluminum, silicon, tin, germanium, indium, antimony and beryllium,"i"ranges from about 70 to 87 atom percent and"j" ranges from about 13 to 30 atom percent. Such materials are conveniently

prepared by rapid quenching from the melt using processing techniques that are now well known in the art.

Metallic glass alloys substantially lack any long-range atomic order and are characterized by x-ray diffraction patterns consisting of diffuse (broad) intensity maxima, qualitatively similar to the diffraction patterns observed for liquids or inorganic oxide glasses. However, upon heating to a sufficiently high temperature, they begin to crystallize with evolution of the heat of crystallization; correspondingly, the x-ray diffraction pattern thereby begins to change from that observed for amorphous materials to that observed for crystalline materials. Consequently, metallic alloys in the glassy form are in a metastable state. This metastable state of the alloy offers significant advantages over the crystalline form of the alloy, particularly with respect to the mechanical and magnetic properties of the alloy.

Use of metallic glasses in magnetic applications has been disclosed in the '513 Patent. However, certain combinations of magnetic properties are needed to realize magnetic components required in modern electronics technology. For example, U. S. Patent No 5,284,528 issued Feb. 8,1994 to Hasegawa et al., addresses such a need. One of the important magnetic properties that affects the performance of a magnetic component used in electrical or electronic devices is called magnetic anisotropy. Magnetic materials are, in general, magnetically anisotropic and the origin of the magnetic anisotropy differs from material to material. In crystalline magnetic materials, one of the crystallographic axes could coincide with the direction of magnetic anisotropy. This magnetically anisotropic direction then becomes the magnetic easy direction in the sense that the magnetization prefers to lie along this direction. Since there are no well- defined crystallographic axes in metallic glass alloys, magnetic anisotropy could be considerably reduced in these materials. This is one of the reasons that metallic glass alloys tend to be magnetically soft, which makes them useful in many magnetic applications. The other important magnetic property is called

magnetostriction, which is defined as a fractional change in physical dimension of a magnetic material when the material is magnetized from the demagnetized state. Thus, magnetostriction of a magnetic material is a function of applied magnetic field. From a practical standpoint, the term"saturation magnetostriction" (X5) is often used. The quantity B5 is defined as the fractional change in length that occurs in a magnetic material when magnetized along its length direction from the demagnetized to the magnetically saturated state. The value of magnetostriction is thus a dimensionless quantity and is given conventionally in units of microstrain (i. e., a fractional change in length, usually parts per million or ppm).

Magnetic alloys of low magnetostriction are desirable for the following reasons: 1. Soft magnetic properties characterized by low coercivity, high permeability, etc. are generally obtained when both the saturation magnetostriction and the magnetic anisotropy of the material become small.

Such alloys are suitable for various soft magnetic applications, especially at high frequencies.

2. When magnetostriction is low and preferably zero, magnetic properties of such near-zero magntostrictive materials are insensitive to mechanical strain. 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 are considerably degraded by even small elastic stresses. Such materials must be carefully annealed after the final forming step.

3. When magnetostriction is near zero, a magnetic material under ac excitation shows a small magnetic loss due to a low coercivity and to reduced energy loss by reduced magneto-mechanical coupling via magnetostriction.

Thus, near-zero magnetostrictive magnetic materials are useful where low magnetic loss and high permeability are required. Near-zero magnetostrictive

material is, therefore, desirable when it is used as a marker in an article surveillance system based on utilizing higher harmonics generated by the marker.

US Patent No. 4,553,136 issued on November 12,1985 to Anderson et al addresses such a case.

There are three well-known crystalline alloys of zero or near-zero magnetostriction: Nickel-iron alloys containing approximately 80 atom percent nickel (e. g."80 Nickel Permalloys"); cobalt-iron alloys containing approximately 90 atom percent cobalt; and iron-silicon alloys containing approximately 6.5 wt. percent silicon. Of these alloys, permalloys have been used more widely than the others because they can be tailored to achieve both zero magnetostriction and low magnetic anisotropy. However, these alloys are prone to be sensitive to mechanical shock, which limits their applications. Cobalt-iron alloys do not provide excellent soft magnetic properties due to their strong negative magnetocrystalline anisotropy. Although some improvements have been made recently in producing iron-based crystalline alloys containing 6.5% silicon [J.

Appl. Phys. Vol. 64, p. 5367 (1988)], wide acceptance of them as a teclmologically competitive material is yet to be seen.

As mentioned above, magnetocrystalline anisotropy is effectively absent in metallic glass alloys due to the absence of crystal structures. It is, therefore, desirable to seek glassy metals with zero magnetostriction. The above mentioned chemical compositions which led to zero or near-magnetostriction in crystalline alloys were thought to give some clues to this effort. The results, however, were disappointing. To this date, only Co-rich and Co-Ni-based alloys with small amount of iron have shown zero or near-zero magnetostriction in glassy states. Examples for these alloys have been reported for Co72Fe3P16B6Al3 (AIP Conference Proceedings, No. 24, pp. 745-746 (1975)) and Co312Fe7. sNi3s. 0B14Sis (Proceedings of 3rd International Conference on Rapidly Quenched Metals, p. 183 (1979)). Co-rich metallic glass alloys with near-zero magnetostriction are commercially available under the trade names of

METGLAS"alloys 2705M and 2714A (Honeywell International Inc) and VITROVAC'@6025 and 6030 (Vacuumschmelze GmbH). These alloys have been used in various magnetic components operated at high frequencies.

Although the above-mentioned Co-Ni based alloy show near-zero magnetostriction, this and similar alloys have never been widely commercialized. Only one alloy (VITROVAC 6006) based on Co-Ni-based metallic glass alloys has been commercially available for anti-theft marker application (U. S. Patent No. 5,037,494). These alloys have saturation magnetic induction below 0.5 T and have limited applications. For example, to compensate the low level of saturation magnetic induction of these alloys, a thin.':' and narrow ribbon is required to achieve a workable anti-theft or electronic article surveillance marker. In addition, this ribbon has to be heat-treated in a magnetic field to realize the desired property as a magnetic marker in electronic article surveillance systems. Such heat-treatment sometimes results in a brittle . ribbon, which makes it difficult to cut the ribbon to a desired length for an electronic article surveillance marker and, in turn, leads to a fragile marker in actual operation. Clearly desirable are new magnetic metallic glass alloys based on Co and Ni that are magnetically more versatile and mechanically more ductile than the existing alloy for applications in electronic article surveillance systems.

SUMMARY OF INVENTION In accordance with the invention, there is provided a magnetic alloy that is at least 70% glassy and which has a low magnetostriction. The metallic glass alloy has the composition CoaNibFecMdBeSifCg where M is at least one element selected from the group consisting of Cr, Mo, Mn and Nb;"a-g"are in atom percent and the sum of"a-g"equals 100;"a"ranges from about 25 to about 60; "b"ranges from about 5 to about 45;"c"ranges from about 6 to about 12;"d" ranges from 0 to about 3;"e"ranges from about 5 to about 25 ;"ranges from 0

to about 15; and"g"ranges from 0 to about 6. The metallic glass alloy has a value of the saturation magnetostriction ranging from about-3 to +3 ppm. The metallic glass alloy is cast by rapid solidification from the melt into ribbon or sheet or wire form. Depending on the need, the metallic glass alloy is heat- treated (annealed) with or without a magnetic field below its crystallization temperature. The metallic glass alloy thus prepared is cut into a desired strip which preferably has a non-linear B-H behavior when measured along the strip's length direction. The strip, whether it is heat-treated or not, is ductile in order to realize a workable : magnetic marker for electronic article surveillance <BR> <BR> <BR> <BR> <BR> applications....,...;..,;:.;.'''' BRIEF DESCRIPTION OF THE DRAWINGS The invention will be more fully understood and further advantages :' become apparent when reference is made to the following detailed description of the invention and the accompanying drawings.

Figs. 1 (A), 1 (B) and 1 (C) are graphs depicting the B-H characteristics of two representative alloys of the present invention DETAILED DESCRIPTION OF THE INVENTION A metallic glass alloy with low saturation magnetostriction provides a number of opportunities for its use in electronic article surveillance applications.

In addition, if the alloy is inexpensive, its technological usefulness will be enhanced. The metallic glass alloy of the present invention has the following composition: CoaNibFecMdBeSifCg, where M is at least one element selected from the group consisting of Cr, Mo, Mn and Nb;"a-g"are in atom percent and the sum of"a-g"equals 100;"a"ranges from about 25 to about 60;"b"ranges from about 5 to about 45;"c"ranges from about 6 to about 12;"d"ranges from 0

to about 3;"e"ranges from about 5 to about 25 ;"franges from 0 to about 15; and"g"ranges from 0 to about 6. The metallic glass alloy has a value of the saturation magnetostriction ranging from about-3 to +3 ppm. The purity of the above composition is that found in normal commercial practice. The metallic glass alloy is conveniently prepared by techniques readily available elsewhere (see, for example, U. S. Pat. No. 3,845,805 issued Nov. 5,1974, and No.

3, 856,513 issued Dec. 24,1974). In general, the metallic glass alloy, in the form ! 5 of. continuous ribbon, wire, etc., is quenched from the melt of a desired composition at a rate of at least about 105 K/s. The sum of boron, silicon and carbon of about 20 atom percent of the total alloy composition is compatible with the alloy's glass forming ability. However, it is preferred that the content of M, i. e. the quantity"d"does not exceed about 2 atom percent by very much when the sum"e+f+g"exceeds 20 atom percent. The metallic glass alloy of the present invention is substantially glassy. That is to say, it is at least 70 % glassy, preferably at least about 95% glassy, and, most preferably, 100 % glassy as determined by x-ray diffractometry, transmission electron microscopy and/or differential scanning calorimetry.

Representative metallic glass alloys prepared in accordance with the present invention are listed in Table I, in which the alloys'as-cast properties such as saturation induction (Bs), saturation magnetostriction (X5), and the first crystallization temperature (Txi) are shown.

TABLE I

Alloy Composition (atom %) Bs (T) #s (ppm) Tx1(°C) 1 Co55 Ni10 Fe10 Mo2 B20 Si3 0.79 2.1 430 2 Co45 Ni25 Fe10 B18 Si2 0.87 0. 3 431 3 Co43 Ni27 Fe10 B18 Si2 0.80 0.4 428 4 Co43 Ni25 Fe10 Mo2 B16 Si2 C2 0.75 0. 9 436 5 Co43 Ni25 Fe10 Mo2 B15 Si2 C30. 73 1.4 429 6 Co41 Ni29 Fe10 B18 Si2 0.82 0.3 425 7 C037. 5 Ni32.5 Fe9 Mo1 B18 Si2 0.62 0.6 427 8 C037. 5 Ni32. 5 Fe9 Mo1 B14 Si6 0.64-1.4 414 9 C037. 5 Ni32. 5 Feo Mol Blo Silo 0.59-0.7 416 10 C037. 5 Nie2. 5 Feg Mol B6 Sil4 0.64-1.2 407 11 Co37 Ni31 Fe12 B18 Si2 0.85 2.1 430 12 Co37 Ni33 Fe10 B18 Si2 0.78 0.4 421 13 Co36 Ni32 Fe12 B18 Si2 0.81 2.3 430 14 Co36 Ni35 Fe8 Mo1 B18 Si2 0.65-1.4 402 15 Co36 Ni35 Fe8 Mol Blo Silo 0.62-0.2 399 16 Co36 Ni35 Fe8 Mo1 B6 Si14 0.56 2.3 388 17 Co35. 4 Ni33.9 Fe7.7 Mo1 B15 Si7 0.57 -0. 3 460 18 Co35. 2 Ni33 Fe7.8 B16 Si8 0.51-0.3 481 19 Co35 Ni33 Fe12 B18 Si2 0.81 1.9 429 20 Co35 Ni34 Fe11 B18 Si2 0.75 1.2 423 21 Co35 Ni35 Fe10 B18 Si2 0.71 0.6 415 22 Co35 Ni34 Fe11 B16 Si4 0.73 1.8 424 23 Co34. 5 Ni33 Fe7.5 Mo1 B16 Si8 0.51 -1. 0 484

24 Co32.5 Ni37.5 Fe9 Mo1 B18 Si2 0.62 0.6 405 25 Co32. 5 Ni37.5 Fe8 Mo1 B14 Si6 0.62 1.4 407 26 C032. 5 Ni37. 5 Fe9 Mo1 B16 Si4 0.52 1.4 391 27 Co31 Ni43Fe7 B17 Si2 0.63-0.9 367 28 Co31 Ni41Fe9 B17 Si2 0.70-1.5 363 29 Co31 Ni41Fe7 B19 Si2 0.56-0.5 412 30 Co31 Ni41Fe7 B17 Si4 0.50-0.3 434 31 Co31 Ni39Fe7 B19 Si4 0.50 0.1 477 32 Co31 Ni39Fe9 B19 Si2 0.65 0.1 412 33 Co31 Ni39Fe9 B17 Si4 0.60-0.8 433 34 Co31 Ni37Fe9 B19 Si4 0.57 0.6 478 35 Co31 Ni38Felo Mo2 B17 Si2 0.60 0.6 427 36 Co3o Ni38Felo Mo2 B18 Si2 0.54 0.8 446 37 Co3o Ni38Felo Mo2 Bi4 Si6 0.57 1.5 433 38 Co30 Ni38Fe10 Mo2 B17 Si2 C1 0.53 0.6 440 39 Co3o Ni38Felo Mo2 B16 Si2 C2 0.57 0.6 433 40 Co30 Ni38Fe10Mo2B15Si2 C3 0.54 0.4 427 41 Co30 Ni41Fe10 Mo2 B15 Si2 0.65 0.7 398 42 Co3o Ni38Felo Mo2 B13 Si2 C5 0.56 0.8 409 43 Co30 Ni37.5 Fe10 Mo2.5 B18 Si2 0. 56-1.0 433 44 Co30 Ni40 Fe9 Mo1 B18 Si2 0.65-1.2 405 45 Co30 Ni40 Fe9 Mo1 B14 Si6 0.58 0.5 411 46 Co30 Ni40 Fe9 Mo1 B16 Si4 0.60-0.3 411 47 Co30 Ni40 Fe8 Mo1 B18 Si3 0.55 0.7 416 48 3Ci. 70. 58 -0. 3 394 49 Co30 Ni40 Fe8 Mo2 B18 Si2 0. 52 0.5 504 50 Co3o Ni4o Fe8 Mo2 B13 Si2 C5 0.51 0.3 409 51 Co30 Ni40 Fe10 B18 Si2 0.69 0.2 416 52 Co3o Ni4o Felo B16 Si2 C2 0.66 0.5 406

53 Co3o Ni4o Felo Bls Si2 C3 0.68 0. 3 401 54 Co3o Ni4o Felo B14 Si2 C4 0.69-0.6 393 55 Co30 Ni40 Fe10 B13 Si2 C5 0.68-1.1 389 56 Co30 Ni40 Fe10 B16 Si4 0.66 0.8 417 57 Co30 Ni40 Fe10 B14 Si4 C2 0.66 0.8 407 58 Co3o Ni4o FeloBl2 Si4 C4 0.64 0.7 394 59 Co30Ni38 Fe10 B20 Si2 0.66 1.0 466 60 Co30 Ni38 Fe10 B18 Si2 C2 0.62 1. 1 481 61 Co3oNi3sFeioBi6Si2C4 0.61 0.6 439 62 Co30 Ni36 Fe10 B22 Si2 0.58 1.0 490 63 Co30 Ni36 Fe10 B18 Si2 C4 0.58 1.0 479 64 Co29Ni45Fe7B17Si2 0.63 1.4 342 65 Co29Ni43Fe7B19Si2 0.55 0. 5 396 66 Co29Ni43Fe7B17Si4 0.53 0.2 403 67 Co29Ni41FeuB19Si2 0.58-0.4 434 68 Co29Ni39Fe9B19Si4 0. 51-0.4 482 69 Co29 Ni40 Fe9 B20 si2 0.58 0.1 454 All the alloys listed in Table I show a saturation induction, Bs, exceeding 0.5 tesla and the saturation magnetostriction within the range between-3 ppm and +3 ppm. It is desirable to have a high saturation induction from the standpoint of the magnetic component's size. A magnetic material with a higher saturation induction results in a smaller component size. In many electronic devices including electronic article surveillance systems currently used, a saturation induction exceeding 0.5 tesla (T) is considered sufficiently high.

Although the alloys of the present invention have the saturation magnetostriction range between-3 ppm and +3 ppm, a more preferred range is between-2 ppm and +2 ppm, and the most preferred is a near-zero value. Examples of the more preferred alloys of the present invention thus include:

Co45Ni25FeloBisSi2, Co43Ni27FeloBlaSi2, C043Ni25FeloMo2B16Si2C2, Co43Ni25FeloMo2B15Si2C3, Co41Ni29Fe10B18Si2, Co37.5Ni32.5Fe9Mo1B18Si2, Co37. 5Ni32. 5Fe9Mo1B14Si6, Co37.5Ni32.5Fe9Mo1B10Si10, Co37.5Ni32.5Fe9Mo1B6Si14, Co37Ni33Fe10B18Si2, Co36Ni35Fe8Mo1B18Si2, Co36Ni35Fe8Mo1B10Si10, C035. 4Ni33. 9Fe7. 7Mo1B15Si7, C035. 2Ni33Fe7. 8Bl6Si8, Co35Ni33Fe12B18Si2, Co35Ni34Fe11B18Si2, Co35Ni35Fe10B18Si2, Co35Ni34Fe11B16Si4, Co34.5Ni33Fe7.5Mo1B16Si8, Co32.5Ni37.5Fe9Mo1B18Si2, Co32.5Ni37.5Fe9Mo1B14Si6, Co32.5Ni37.5Fe9Mo1B6Si14, Co31Ni43Fe7B17Si2, Co31Ni41Fe9B17Si2, C031Ni4lFe7B19Si2, Co31Ni41Fe7B17Si4, C03lNi39Fe7Bl9Si4, C031Ni39Fe9Bl9Si2, Co31Ni39Fe9B17Si4, C031Ni39Fe9Bl9Si2, Co31Ni38FeloMo2B17Si2, Co3oNi38FeloMo2B18Si2, Co30Ni38Fe10Mo2B17Si2C1, C030Ni38FeloMo2B16Si2C2, C030Ni38FeloMo2BI5Si2C3, Co30Ni4lFelOMo2B15Si2, Co30Ni38Fe10Mo2B14Si6, C03oNi38FeloM02B13Si2C5, Co30Ni4oFe8Mo2B18Si2, Co30Ni40Fe8Mo2B13Si2C5, Co30Ni40Fe10B18Si2, Co30Ni40Fe9Mo1B18Si2, Co30Ni40Fe01B15Si2C3, Co30Ni40Fe10B14Si2C4, Co30Ni40Fe10B13Si2C5, Co30Ni40Fe10B16Si4, Co30Ni40Fe10B14Si4C2, Co30Ni40Fe10B12Si4C4, Co30Ni40Fe10B20Si2, Co30Ni38Fe10B18Si2C2, Co30Ni36Fe10B16i2C4, Co30Ni36Fe10B22Si2, Co30Ni34Fe10B18Si2C4, Co30Ni40Fe9Mo1B18Si2, Co30Ni40Fe9Mo1B14Si6, C03oNi4oFe9Mo1B16Si4, Co3oNi37. 5FeloMo2. 5B18Si2, Co3oNi4oFe8Mo1B18Si3, C030Ni4oFe8MOIB17Si2. 3CI. 7, C029Ni43Fe7Bl9Si2, C029Ni4lFe9Bl9Si2, Co29Ni43Fe7B17Si4, Co29Ni45Fe7B17Si2, Co29Ni39Fe9B19Si4 and Co29Ni40Fe9B20si2.

In electronic article surveillance systems utilizing higher harmonics, the magnetic marker must possess a non-linear B-H behavior with B-H squareness ratios exceeding about 0.5 and preferrably exceeding about 0.75. Fig. l represents typical B-H loops well-known to those skilled in the art. The vertical axis is scaled to the magnetic induction B in tesla (T) and the horizontal axis is scaled to

the applied magnetic field H in amperes/meter (A/m). Fig. 1A corresponds to the case where a marker strip is in the as-cast condition. Some of the metallic glass alloys in Table 1 exhibit rectangular B-H behaviors similar to Fig. 1 in the as-cast condition and are most suited for use as a magnetic marker since they are ductile and therefore easily cut and fabricated.

Heat treatment or annealing of the metallic glass alloy of the present invention favorably modifies the magnetic properties of the alloy. The choice of the annealing conditions differs depending on the required performance of the envisioned component. Since a non-linear B-H behavior is required of a magnetic marker in electronic article surveillance systems, the annealing condition then may require a magnetic field applied along the direction of the marker strip's length direction. Fig. 1B corresponds to the case where the marker strip is heat-treated with a magnetic field applied along the strip's length direction. It has been noted that the B-H loop is highly non-linear and square.

This kind of behavior is very well suited for the alloy to be used as a magnetic marker in electronic article surveillance systems. Specific annealing conditions must be found for different types of applications using the metallic glass alloys of the present invention. Such examples are given below: EXAMPLES 1. Sample Preparation The metallic glass alloys listed in Table I were rapidly quenched with a cooling rate of approximately 106 K/s from the melt following the techniques taught by Chen et al in U. S. Patent 3,856,513. The resulting ribbons, typically 10 to 30 pm thick and 0.5 to 2.5 cm wide, were determined to be free of significant crystallinity by x-ray diffractometry (using Cu-Ka radiation) and

differential scanning calorimetry. The metallic glass alloys in the ribbon form were strong, shiny, hard and ductile.

2. Magnetic Measurements The saturation magneization, Ms, 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) which were placed in a sample holder with their plane parallel to the applied field reaching a maximum of about 800 kA/m (or 10 kOe). The saturation induction Bs (= 4sMsD) was then calculated using the measured mass density D.

The saturation magnetostriction was measured on a piece of ribbon sample (approximately 3 mm x 10 mm in size) which was attached to a metallic strain gauge. The sample with the strain gauge was placed in a magnetic field of about 40 kA/m (500 Oe) The strain change in the strain gauge was measured by a resistance bridge circuit described elsewhere [Rev. Scientific Instrument, Vol. 51, p. 382 (1980)] when the field direction was changed from the sample length direction to the width direction. The saturation magnetostriction was then determined from the formula B5 = 2/3 (difference in the strain between the two directions).

The ferromagnetic Curie temperatue, Of, was measured by an inductance method and also monitored by differential scanning calorimetry, which was used primarily to determine the crystallization temperatures. Depending on the chemistry, crystallization sometimes takes place in more than one step. Since the first crystallization temperature is more relevant to the present application, the first crystallization temperatures of the metallic glass alloys of the present invention are listed in Table I.

Continuous ribbons of the metallic glass alloys prepared in accordance with the procedure described in Example 1 were wound onto bobbins (3.8 cm O. D.) to form magnetically closed toroidal sample. Each sample toroidal core contained from about 1 to about 30 g of ribbon and had primary and secondary copper windings which were wired to a commercially available B-H loop tracer to obtain B-H hysteresis loops of the kind shown in Fig. 1.

Continuous ribbons of the metallic glass alloys prepared in accordance with the procedure described in Example 1 were slit to widths ranging from about 1 mm to about 3 mm and cut into strips of lengths of about 76 mm. Each strip was placed in an exciting ac field at a fundamental frequency and its higher harmonics response was detected by a coil containing the strip. The harmonics response signal detected in the coil was monitored by a digital voltmeter and by a conventional oscilloscope.

3. Magnetic Harmonic Markers using As-cast Alloys Toroidal cores prepared in accordance with Example 2 using as-cast alloys of the present invention were tested. The results of dc coercivity and dc B-H squareness ratio of Alloys 2,3,6,20,21,39,41,49,56,57, and 61 of Table I are given in Table II.

Table II Alloy No. dc Coercivity (A/m) dc Squareness Ratio 2 1.8 0.93 3 3.1 0.88 6 2.4 0.90 20 2.6 0.66 21 2.6 0.86 39 2.2 0.72

41 2.3 0. 94 49 0.6 0.88 56 1.5 0.50 57 1.8 0.92 61 3.2 0.51 Low coercivities and B-H squareness ratios exceeding about 0.5 indicate that the alloys of the present invention in their as-cast conditions are suited for variety of magnetic applications including electronic article surveillance, magnetic sensors, power electronics and the like. Those alloys with higher squareness ratios are especially suited for use in electronic article surveillance systems based on magnetic harmonics. Some of these as-cast strips were evaluated according to the measurement technique described in Example 2 and the results are summarized in Table III below.

Table in The as-cast strips made from Alloy 20,21,67, and 69 of Table I and control strips were excited at a fundamental frequency of 2.4 kHz and their 25th harmonic signal responses were detected. The excitation level was kept constant and the signal detected in a 524-turn coil was compared. The control strip was a 2 mm wide, 76-mm long strip made of METGLASR 2705M alloy and taken out of a commercially available marker widely used in video rental stores. For comparison purpose, 1 mm and 3 mm wide strips of METGLAS (k2705M alloy were prepared and tested.

Alloy Width (mm) 25th Harmonic Voltage (mV) Control 3 150i10

Control 2 160~10 Control 1 19010 No. 20 3 230~10 No. 21 3 220i10 No. 67 3 240~10 No. 69 3 240A10 No. 67 1 290t10 No. 69 1 290~10 The data shown above indicate that the harmonic markers made from the strips of the as-cast alloys of the present invention perform equally or better than those commercially available.

4. Magnetic Harmonic Markers using Annealed Alloys Toroidal cores prepared in accordance with the procedure of Example 2 were annealed with a magnetic field of 800 A/m applied along the circum- ference direction of the toroids. The results of dc B-H hysteresis loops taken on some of the alloys from Table 1 are listed in Table IV.

Table IV Coercivity He and B-H squareness ratio (Br/Bs where Br is the remanent induction) for some of the metallic glass alloys of Table I. The alloys were annealed at 320°C for 2 hours with a dc magnetic field of 800 A/m applied along the core circumference direction.

Alloy No He (A/m) B-H Squareness Ratio 1 1. 3 0.93 2 2.3 0.96 5 1.1 0.93 6 3.6 0.93 11 2.0 0.98 19 1.2 0.95 35 1.2 0.93 40 0.6 0.87 41 2.4 0.95 49 0.4 0.88 51 1.0 0.93 54 1.6 0.89 57 1.0 0.93 These results show that the metallic glass alloys of the present invention achieve a high dc B-H squareness ratio exceeding 0.85 with low coercivities of less than 4 A/m when annealed with a dc magnetic field applied along the direction of the magnetic excitation, indicating further that these alloys are suited for use as markers in electronic article surveillance systems utilizing magnetic harmonics.

Table V summarizes the results of the harmonic response of the strips from Table I which were heat-treated at 370 °C for 1.5 hours with a magnetic field of 10 Oe applied along the strip's length direction in accordance with Example 2.

Table V Heat-treated strips of Alloy No. 21,67 and 69 from Table I were excited at 2.4 kHz and its 25t1' harmonic response signal. The measurement conditions are the same as those given in the caption of Table III.

Alloy Width (mm) 25th Harmonic Response (mV) No. 21 3 130~10 No. 67 3 180A10 No. 69 3 170i10 No. 67 1 200~10 No. 69 1 195i10 The data given in Table V indicate that heat-treated alloys of the present invention perform equally or better than the commercially available alloy (control alloy in Table 110 when used as markers of electronic article surveillance systems utilizing magnetic harmonics.

Having thus described the invention rather full detail, it will be understood that this detail need not be strictly adhered to but that further changes and modifications may suggest themselves to one skilled in the art all falling within the scope of the invention as defined by the subjoined claims.