CA1145162A - Iron-boron silicon ternary amorphous alloys - Google Patents
Iron-boron silicon ternary amorphous alloysInfo
- Publication number
- CA1145162A CA1145162A CA000340407A CA340407A CA1145162A CA 1145162 A CA1145162 A CA 1145162A CA 000340407 A CA000340407 A CA 000340407A CA 340407 A CA340407 A CA 340407A CA 1145162 A CA1145162 A CA 1145162A
- Authority
- CA
- Canada
- Prior art keywords
- iron
- boron
- alloys
- alloy
- atom percent
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Soft Magnetic Materials (AREA)
Abstract
RD-11,433 ABSTRACT OF THE DISCLOSURE
Iron-boron-silicon ternary amorphous alloys having high saturation magnetization, high crystallization temperature and low coercivity are provided. Such alloys provide superior performance when used in electrical apparatus such as motors and transformers.
Iron-boron-silicon ternary amorphous alloys having high saturation magnetization, high crystallization temperature and low coercivity are provided. Such alloys provide superior performance when used in electrical apparatus such as motors and transformers.
Description
RD-11,433 1~ ~51~2 Th~ present invention relates generally to the metal alloy art and is more particularly concerned with novel amorphous metal alloys having a unique combination of magnetic and physical properties, and is further concerned with ribbons and other useful articles made therefrom.
While it has been recognized by those skilled in the art that amorphous metals with high saturation magnetization might be used to advantage in electrical apparatus such as distribution and power transformers, such alloys are lacking in necessary ductility and stability for this purpose. Thus, the iron-rich alloy Fe80B20 has a 4 ~ Ms of approximately 16,000 Gauss but begins to crystallize within two hours at about 325C and is quite difficult to produce in ductile ribbon form for electrical machinery apparatus. Other amorphous alloys known heretofore have somewhat greater stability and adequate ductility for this purpose, but their saturation magnetization is too low.
This invention is based upon the discovery that a very narrow range of iron, boron and silicon amorphous alloys have both the desired magnetization and other pro-perties for superior performance in electrical apparatus such as motors and transformers. Consequently it is now possible by means of this invention to provide an amorphous metal in the form of a ribbon sufficiently ductile to be readily used in electrical apparatus construction which has good magnetic properties and elevated temperature stability.
FIGURE 1 is a ternary diagram plotting saturation ~ magnetization fo~ a variety o$ iron, boron and silicon alloys at room temperature (30C~.
FIGURE 2 i5 a ternary diagram plotting coercivity for a variety o$ iron, boron and silicon alloys;
FIGURE 3 is a ternary diagram plotting the ~`
- - . :: . :
~14S~2 RD-11,433 crystallizatlon temperature for said alloys and FIGURE 4 is a composite of the saturation magnetization contour lines of FIGURE 1 and the coercivity contour lines of FIGURE 2 with the 320C contour line from Figure 3 superimposed thereon. Shaded region A, B, C, D, E, F, A designates those iron-boron-silicon ternary amorphous metal alloy compositions simultaneously exhibiting the properties of saturation magnetization of at least about 174 emu/g at about 30C, intrinsic coercivity after annealing of less than about 0.03 oersteds and crystallization temperature of at least about 320 C.
Referring now to the drawings and particularly FIGURE
1 it can be seen that a superior group of alloys is formed from all alloys of iron, boron and silicon ~ithin the broken lines, i.e., of from 80 atom percent iron, 19 atom percent boron and 1 atom percent silicon to 81 3/4 atom percent iron, 17 1/4 atom percent boron and 1 atom percent silicon to 81 3/4 atom percent iron, 12 1/4 atom percent boron and 6 atom percent silicon to 82 1/4 atom percent iron, 11 3/4 atom percent boron and 6 atom percent silicon.
However, this designation includes only part of the spectrum of iron-boron-silicon amorphous metal alloys exhibitin~
the unique confluence of properties comprising this invention. This complete ~pectrum is described hereinafter in connection with FIGuRE 4.
In FIGURE 1 saturation magnetizations are plotted for a variety of amorphous alloys. Magnetizations at room temperature and below Were determined on small weighed specimens in a vibrating sample magnetometer to a maximum field of 20 KOe. Results were extxapolated to H - oo using a l/H function. ~alues above room temperature were obtained from the reIative magnetization curves normalized ~ ~ ~ 5 ~ z RD-11,433 to the value of magnetization at room temperature. From an examination of the diagram it can be seen that the alloys of the invention have a desirable saturation magnetization of 178 emu/g at room temperature (30C~.
In FIGURE 2 the intrinsic coercivity is plotted for a number of iron-boron-silicon alloys which was determined on 10 cm. long ribbons set into a 20 cm. long solenoid which was then annealed for 120 min. at a few degrees centrigrade below the crystallization temperatures shown in FIGURE 3. A small sense coil was connected to an integrating flux meter and the magnetization vs filed was then displayed on an X-Y recorder as the field was slowly varied. From an examination of the diagram it can be seen that the lowest coercivity of 0.02 Oe is found with the alloys having the desirable high saturation magnetization of 178 emu/g reported in FIGURE 1.
In FIGURE 3 crystallization temperatures are reported as determined by noting the temperature at which the coercivity starts to increase after 2 hour exposures at increasing temperature. From an examination of the diagrams it can be seen that the alloys found to have high saturation magnetization and low coercivity are also found to have acceptably high crystallization temperatures.
Crystallization temperatures up to 340 C are obtained for the 6 atom percent silicon alloys compared to 310-315 C
for the Fe82B18 alloy. This is desirable as it permits the allo~ to be annealed to relieve the stresses and reduce the initial high coercive field without permitting the amorphous alloy to crystallize and lose its desirable magnetic ~ualities. Thus ~ith the alloys of the invention it is possible to anneal frQm above about 320 C ~ithout cr~stallization occurring. Figure 4 presents a composite ~1~5~ RD-11,433 of the gradient lines of FIGURES 1 and 2 with the 320 C
contour line of FIGURE 3 added thereto. It is this unification of data, which focuses on the discovery wherehy for the first time those amorphous alloys of the iron-boron-silicon system have been identified in which there is a confluence of the properties of high room temperature saturation magnetization, high crystallization temperature and low coercivity. As can be seen from FIGURE 1, there is a sharp increase in the steepness of the gradient of the saturation magnetization contour lines from the value of 174 emu/g to higher ~alues. It was never previously recognized that amorphous alloys in this system could be found with the unusual combination of properties of saturation magnetization at room temperature (i.e. about 30 C) of at least about 174 emu/g, intrinsic coercivity of less than about 0.03 oersteds and crystallization temperature of at least about 320C. Alloys exhibiting this unusual collection of properties are found in the shaded area bounded by the gradient lines of coercivity, saturation magnetization and crystallization temperature whose intersections are labeled ~, B, C, D, E, F. Even more effective alloy COmpQsitiOnS
are located in the area designated a, b, c, d defined by the compositions 81 atom percent iron, 16 atom pecent boron and 3 atom percent silicon (point a); 81 3/4 atom percent iron, 15 1/4 atom percent boron and 3 atom percent silicon (point d~; 81 1/2 atom percent iron, 13 1/2 atom percent horon and 5 atom percent silicon (point b~, and 82 atom pexcent iron, l3 atom percent boron and S atom percent 81.3 15.7Si3 and Fegl 7B13-3Si5 as well as the aptimum composition, which has an iron content of 81 1/2 atom percent, a horQn cantent of 14 1/2 atQm percent and a silicon content o~ 4 atom percent are part of area a,b,c,d. --~ S~6Z RD-11,433 In practicing this invention, novel alloys defined above and claimed herein are prepared suitable by mixing together the alloy constituents in the required proportions in the form of powders and then melting the mixture to provide molten alloy for casting to ribbon of the desired dimensions. The casting is preferably carried out through the use of the method disclosed and claimed in Canadian application Serial No. 321,822, filed Fèbruary 16, 1979, in the name of John L. Walter and assigned to the lQ assi~nee hereof. The apparatus described in that application as implementing the therein-claimed method may likewise be used to provide long lengths of ribbons of this invention of uniform ~idth and thickness and smooth edges and surfaces.
Cooling is carried out in the casting operation at a rate sufficient to produce amorphous material.
While variations in melting point temperatures between alloys of this invention may impose requirements which vary with respect to alloy melting and casting operations, the prepaXation and processing of these alloys can be carried out with uniformly satisfactory results by following the above procedure and using the described equipment. In other ~ords, the results of this invention are reproducible in a substantially routine manner so long as the compositional limitations stated above and in the appended claims are strictly observed in the preparation of the alloys.
Ribbons of amorphous alloys claimed herein and havin~ the properties detailed in FIGURES 1, 2 and 3 are made by directing a stream of the alloy onto the surface of a rapi:dl~ revolYing chill roll or dxum as described in EXAMPLE 1 of Canadian p~tent application ~erial No.321,822, noted above.
A t~pical ribbon has a thickness of O.Q025 cm and is 0.13 cm.
wide. The amorphous nature of the xesulting ribbon is-~ 5~2 RD-11,433 confirmed by X-ray diffraction, differential scanning calorimetry, and by magnetic and physical property measurements. When the segments are annealed in purified nitrogen for two hours at temperatures ranging from 100C
to 400C the crystallization temperature is taken as that temperature, for the 2-hr. anneal, at which the coercive force abruptly increases.
To prepare a transformer or motor stator, strips of the aforesaid alloy about 1/2" wide and 2 mils thick can be coated with a binder such as polyamide-imide and the strips placed 6 layers deep in a non-magnetic die cavity of stainless steel lined with Teflon-coated a-luminum with alternating layers at 90. The strips are held in place by means of permanent magnets placed under the die and the composite pressed at 2000 psi and 330C for 2 minutes after allowing the die to preheat to 330C for a few minutes without pressure to equilibrate and drive out excessive air and water from the die and ribbon. The composite is then annealed at 325C for 2 hours and found to have a low coercive force and high saturation magnetization.
Other composites are formed with or without a binder with similar results. Other suitable binders include the epoxies, polyamide-imides, cyanoacrylates, and phenolics.
The binder should have a coefficient of thermal expansion compatible with the metal ribbon, be electrically insulating, cure rapidly and be able to meet the thermal requirements of the intended application and annealing if required. In some applications there are further re~uirements such as being compatible with commercial refrigements when used for air conditioning compressor motors.
The above method for preparing a stator is described and claimed in United States patent 4,201,837 11~51~2 RD-ll,433 issued May 6, 1980 to J.H. Lupinski and assigned to the present assignee.
To prepare a wound-type transformer the amorphous metal foil, with widths, for example, up to 6 inches wide, may be wound on a mandrel with a circular or rectangular cross-section. The number of turns wound onto the mandrel, and the width of the tape, will depend on the transformer rating.
It will be understood by those skilled in the art that slight but obvious modifications can be made which will fall within the scope of the invention. For example, an article of manufacture claimed herein may contain a minor amount of crystalline material which will not seriously impair its desirable properties. Accordingly, depending upon the particular article of manufacture and its intended use, the article may contain up to 10% of crystalline material.
Consequently the application is intended to be limited only by the appended claims.
While it has been recognized by those skilled in the art that amorphous metals with high saturation magnetization might be used to advantage in electrical apparatus such as distribution and power transformers, such alloys are lacking in necessary ductility and stability for this purpose. Thus, the iron-rich alloy Fe80B20 has a 4 ~ Ms of approximately 16,000 Gauss but begins to crystallize within two hours at about 325C and is quite difficult to produce in ductile ribbon form for electrical machinery apparatus. Other amorphous alloys known heretofore have somewhat greater stability and adequate ductility for this purpose, but their saturation magnetization is too low.
This invention is based upon the discovery that a very narrow range of iron, boron and silicon amorphous alloys have both the desired magnetization and other pro-perties for superior performance in electrical apparatus such as motors and transformers. Consequently it is now possible by means of this invention to provide an amorphous metal in the form of a ribbon sufficiently ductile to be readily used in electrical apparatus construction which has good magnetic properties and elevated temperature stability.
FIGURE 1 is a ternary diagram plotting saturation ~ magnetization fo~ a variety o$ iron, boron and silicon alloys at room temperature (30C~.
FIGURE 2 i5 a ternary diagram plotting coercivity for a variety o$ iron, boron and silicon alloys;
FIGURE 3 is a ternary diagram plotting the ~`
- - . :: . :
~14S~2 RD-11,433 crystallizatlon temperature for said alloys and FIGURE 4 is a composite of the saturation magnetization contour lines of FIGURE 1 and the coercivity contour lines of FIGURE 2 with the 320C contour line from Figure 3 superimposed thereon. Shaded region A, B, C, D, E, F, A designates those iron-boron-silicon ternary amorphous metal alloy compositions simultaneously exhibiting the properties of saturation magnetization of at least about 174 emu/g at about 30C, intrinsic coercivity after annealing of less than about 0.03 oersteds and crystallization temperature of at least about 320 C.
Referring now to the drawings and particularly FIGURE
1 it can be seen that a superior group of alloys is formed from all alloys of iron, boron and silicon ~ithin the broken lines, i.e., of from 80 atom percent iron, 19 atom percent boron and 1 atom percent silicon to 81 3/4 atom percent iron, 17 1/4 atom percent boron and 1 atom percent silicon to 81 3/4 atom percent iron, 12 1/4 atom percent boron and 6 atom percent silicon to 82 1/4 atom percent iron, 11 3/4 atom percent boron and 6 atom percent silicon.
However, this designation includes only part of the spectrum of iron-boron-silicon amorphous metal alloys exhibitin~
the unique confluence of properties comprising this invention. This complete ~pectrum is described hereinafter in connection with FIGuRE 4.
In FIGURE 1 saturation magnetizations are plotted for a variety of amorphous alloys. Magnetizations at room temperature and below Were determined on small weighed specimens in a vibrating sample magnetometer to a maximum field of 20 KOe. Results were extxapolated to H - oo using a l/H function. ~alues above room temperature were obtained from the reIative magnetization curves normalized ~ ~ ~ 5 ~ z RD-11,433 to the value of magnetization at room temperature. From an examination of the diagram it can be seen that the alloys of the invention have a desirable saturation magnetization of 178 emu/g at room temperature (30C~.
In FIGURE 2 the intrinsic coercivity is plotted for a number of iron-boron-silicon alloys which was determined on 10 cm. long ribbons set into a 20 cm. long solenoid which was then annealed for 120 min. at a few degrees centrigrade below the crystallization temperatures shown in FIGURE 3. A small sense coil was connected to an integrating flux meter and the magnetization vs filed was then displayed on an X-Y recorder as the field was slowly varied. From an examination of the diagram it can be seen that the lowest coercivity of 0.02 Oe is found with the alloys having the desirable high saturation magnetization of 178 emu/g reported in FIGURE 1.
In FIGURE 3 crystallization temperatures are reported as determined by noting the temperature at which the coercivity starts to increase after 2 hour exposures at increasing temperature. From an examination of the diagrams it can be seen that the alloys found to have high saturation magnetization and low coercivity are also found to have acceptably high crystallization temperatures.
Crystallization temperatures up to 340 C are obtained for the 6 atom percent silicon alloys compared to 310-315 C
for the Fe82B18 alloy. This is desirable as it permits the allo~ to be annealed to relieve the stresses and reduce the initial high coercive field without permitting the amorphous alloy to crystallize and lose its desirable magnetic ~ualities. Thus ~ith the alloys of the invention it is possible to anneal frQm above about 320 C ~ithout cr~stallization occurring. Figure 4 presents a composite ~1~5~ RD-11,433 of the gradient lines of FIGURES 1 and 2 with the 320 C
contour line of FIGURE 3 added thereto. It is this unification of data, which focuses on the discovery wherehy for the first time those amorphous alloys of the iron-boron-silicon system have been identified in which there is a confluence of the properties of high room temperature saturation magnetization, high crystallization temperature and low coercivity. As can be seen from FIGURE 1, there is a sharp increase in the steepness of the gradient of the saturation magnetization contour lines from the value of 174 emu/g to higher ~alues. It was never previously recognized that amorphous alloys in this system could be found with the unusual combination of properties of saturation magnetization at room temperature (i.e. about 30 C) of at least about 174 emu/g, intrinsic coercivity of less than about 0.03 oersteds and crystallization temperature of at least about 320C. Alloys exhibiting this unusual collection of properties are found in the shaded area bounded by the gradient lines of coercivity, saturation magnetization and crystallization temperature whose intersections are labeled ~, B, C, D, E, F. Even more effective alloy COmpQsitiOnS
are located in the area designated a, b, c, d defined by the compositions 81 atom percent iron, 16 atom pecent boron and 3 atom percent silicon (point a); 81 3/4 atom percent iron, 15 1/4 atom percent boron and 3 atom percent silicon (point d~; 81 1/2 atom percent iron, 13 1/2 atom percent horon and 5 atom percent silicon (point b~, and 82 atom pexcent iron, l3 atom percent boron and S atom percent 81.3 15.7Si3 and Fegl 7B13-3Si5 as well as the aptimum composition, which has an iron content of 81 1/2 atom percent, a horQn cantent of 14 1/2 atQm percent and a silicon content o~ 4 atom percent are part of area a,b,c,d. --~ S~6Z RD-11,433 In practicing this invention, novel alloys defined above and claimed herein are prepared suitable by mixing together the alloy constituents in the required proportions in the form of powders and then melting the mixture to provide molten alloy for casting to ribbon of the desired dimensions. The casting is preferably carried out through the use of the method disclosed and claimed in Canadian application Serial No. 321,822, filed Fèbruary 16, 1979, in the name of John L. Walter and assigned to the lQ assi~nee hereof. The apparatus described in that application as implementing the therein-claimed method may likewise be used to provide long lengths of ribbons of this invention of uniform ~idth and thickness and smooth edges and surfaces.
Cooling is carried out in the casting operation at a rate sufficient to produce amorphous material.
While variations in melting point temperatures between alloys of this invention may impose requirements which vary with respect to alloy melting and casting operations, the prepaXation and processing of these alloys can be carried out with uniformly satisfactory results by following the above procedure and using the described equipment. In other ~ords, the results of this invention are reproducible in a substantially routine manner so long as the compositional limitations stated above and in the appended claims are strictly observed in the preparation of the alloys.
Ribbons of amorphous alloys claimed herein and havin~ the properties detailed in FIGURES 1, 2 and 3 are made by directing a stream of the alloy onto the surface of a rapi:dl~ revolYing chill roll or dxum as described in EXAMPLE 1 of Canadian p~tent application ~erial No.321,822, noted above.
A t~pical ribbon has a thickness of O.Q025 cm and is 0.13 cm.
wide. The amorphous nature of the xesulting ribbon is-~ 5~2 RD-11,433 confirmed by X-ray diffraction, differential scanning calorimetry, and by magnetic and physical property measurements. When the segments are annealed in purified nitrogen for two hours at temperatures ranging from 100C
to 400C the crystallization temperature is taken as that temperature, for the 2-hr. anneal, at which the coercive force abruptly increases.
To prepare a transformer or motor stator, strips of the aforesaid alloy about 1/2" wide and 2 mils thick can be coated with a binder such as polyamide-imide and the strips placed 6 layers deep in a non-magnetic die cavity of stainless steel lined with Teflon-coated a-luminum with alternating layers at 90. The strips are held in place by means of permanent magnets placed under the die and the composite pressed at 2000 psi and 330C for 2 minutes after allowing the die to preheat to 330C for a few minutes without pressure to equilibrate and drive out excessive air and water from the die and ribbon. The composite is then annealed at 325C for 2 hours and found to have a low coercive force and high saturation magnetization.
Other composites are formed with or without a binder with similar results. Other suitable binders include the epoxies, polyamide-imides, cyanoacrylates, and phenolics.
The binder should have a coefficient of thermal expansion compatible with the metal ribbon, be electrically insulating, cure rapidly and be able to meet the thermal requirements of the intended application and annealing if required. In some applications there are further re~uirements such as being compatible with commercial refrigements when used for air conditioning compressor motors.
The above method for preparing a stator is described and claimed in United States patent 4,201,837 11~51~2 RD-ll,433 issued May 6, 1980 to J.H. Lupinski and assigned to the present assignee.
To prepare a wound-type transformer the amorphous metal foil, with widths, for example, up to 6 inches wide, may be wound on a mandrel with a circular or rectangular cross-section. The number of turns wound onto the mandrel, and the width of the tape, will depend on the transformer rating.
It will be understood by those skilled in the art that slight but obvious modifications can be made which will fall within the scope of the invention. For example, an article of manufacture claimed herein may contain a minor amount of crystalline material which will not seriously impair its desirable properties. Accordingly, depending upon the particular article of manufacture and its intended use, the article may contain up to 10% of crystalline material.
Consequently the application is intended to be limited only by the appended claims.
Claims (4)
1. An iron-boron-silicon amorphous metal alloy simultaneously having values of saturation magnetization at about 30°C of at least about 174 emu/g, intrinsic coercivity of less than about 0.03 oersted and crystallization temperature of at least about 320°C, said alloy consisting essentially of iron, boron and silicon and having a composition in the region A, B, C, D, E, F, A of FIG. 4, boron being present in an amount greater than 15 atom percent.
2. The alloy of claim 1, of the formula Fe81B16Si3.
3. The alloy of claim 1, of the formula Fe81.3B15.7Si3.
4. The alloy of claim 1, of the formula Fe81.75B15.25Si3.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US964,621 | 1978-11-29 | ||
| US05/964,621 US4217135A (en) | 1979-05-04 | 1978-11-29 | Iron-boron-silicon ternary amorphous alloys |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1145162A true CA1145162A (en) | 1983-04-26 |
Family
ID=25508779
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000340407A Expired CA1145162A (en) | 1978-11-29 | 1979-11-22 | Iron-boron silicon ternary amorphous alloys |
Country Status (7)
| Country | Link |
|---|---|
| JP (1) | JPS5594460A (en) |
| CA (1) | CA1145162A (en) |
| DE (1) | DE2947802A1 (en) |
| ES (1) | ES8102596A1 (en) |
| FR (1) | FR2442894A1 (en) |
| GB (1) | GB2038358B (en) |
| PH (1) | PH14784A (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3165416D1 (en) * | 1980-12-29 | 1984-09-13 | Allied Corp | Amorphous metal alloys having enhanced ac magnetic properties |
| US6296948B1 (en) * | 1981-02-17 | 2001-10-02 | Ati Properties, Inc. | Amorphous metal alloy strip and method of making such strip |
| JPS58173059A (en) * | 1982-03-03 | 1983-10-11 | Unitika Ltd | Production of fine metallic wire |
| AU9179282A (en) * | 1982-05-27 | 1983-12-01 | Allegheny Ludlum Steel Corp. | Amorphous, magnetic iron base - boron silicon alloy |
| JPS63186560A (en) * | 1987-05-15 | 1988-08-02 | Toshiba Corp | Voltage resonance type high frequency switching circuit |
| ATE429522T1 (en) * | 2002-01-16 | 2009-05-15 | Nakagawa Special Steel Co Ltd | MAGNETIC BASE MATERIAL, LAMINATE MADE OF MAGNETIC BASE MATERIAL AND PRODUCTION PROCESS THEREOF |
| KR20160020500A (en) | 2013-07-30 | 2016-02-23 | 제이에프이 스틸 가부시키가이샤 | Thin amorphous iron alloy strip |
| JP6478061B2 (en) | 2016-04-04 | 2019-03-06 | Ｊｆｅスチール株式会社 | Amorphous alloy ribbon |
| CN107267889B (en) * | 2017-06-14 | 2019-11-01 | 青岛云路先进材料技术股份有限公司 | A kind of Fe-based amorphous alloy and preparation method thereof with low stress sensibility |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| NL182182C (en) * | 1974-11-29 | 1988-01-18 | Allied Chem | DEVICE WITH AMORPHIC METAL ALLOY. |
| US4188211A (en) * | 1977-02-18 | 1980-02-12 | Tdk Electronics Company, Limited | Thermally stable amorphous magnetic alloy |
| GB2023653A (en) * | 1978-04-20 | 1980-01-03 | Gen Electric | Zero Magnetostriction Amorphous Alloys |
| GB2023173B (en) * | 1978-04-20 | 1982-06-23 | Gen Electric | Amorphous alloys |
-
1979
- 1979-11-06 GB GB7938391A patent/GB2038358B/en not_active Expired
- 1979-11-22 CA CA000340407A patent/CA1145162A/en not_active Expired
- 1979-11-27 JP JP15251879A patent/JPS5594460A/en active Pending
- 1979-11-28 DE DE19792947802 patent/DE2947802A1/en active Granted
- 1979-11-28 ES ES486427A patent/ES8102596A1/en not_active Expired
- 1979-11-28 PH PH23338A patent/PH14784A/en unknown
- 1979-11-29 FR FR7929369A patent/FR2442894A1/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| FR2442894B1 (en) | 1985-04-19 |
| ES486427A0 (en) | 1981-01-16 |
| GB2038358A (en) | 1980-07-23 |
| DE2947802C2 (en) | 1989-03-09 |
| DE2947802A1 (en) | 1980-06-12 |
| ES8102596A1 (en) | 1981-01-16 |
| GB2038358B (en) | 1982-12-08 |
| JPS5594460A (en) | 1980-07-17 |
| PH14784A (en) | 1981-12-09 |
| FR2442894A1 (en) | 1980-06-27 |
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| MKEX | Expiry |