Patent Grant
10927440
The disclosure is directed to Zr—Ti—Cu—Ni—Al metallic glasses having a high glass forming ability and a high thermal stability of the supercooled liquid against crystallization.
U.S. Pat. No. 5,032,196, entitled “Amorphous Alloys Having Superior Processability,” the disclosure of which is incorporated herein by reference in its entirety, discloses ternary Zr—Cu—Al and quaternary Zr—Cu—Ni—Al alloys capable of forming glasses in geometries with thin lateral dimensions (i.e. where the thickness is on the order of micrometers), where the Zr atomic concentration varies in the range of 25 to 85 percent, the combined Ni and Cu atomic concentration varies in the range of 5 to 70 percent, and the Al atomic concentration varies in the range of up to 35 percent. The patent also discloses that the Zr—Cu—Al and Zr—Cu—Ni—Al alloys may optionally contain Ti in an atomic concentration of up to 5 percent without altering the disclosed effects of the alloys. The patent presents several examples of micrometer-thick amorphous Zr—Cu—Al ribbons where the thermal stability of the supercooled liquid (i.e. the difference between the crystallization and glass transition temperatures) at an unspecified heating rate ranges from 0° C. to 91° C. between the various compositions.
U.S. Pat. No. 5,735,975, entitled “Quinary Metallic Glass Alloys,” the disclosure of which is incorporated herein by reference in its entirety, discloses quinary Zr—Ti—Cu—Ni—Al alloys capable of forming glasses in bulk geometries (i.e. where the thicknesses is on the order of millimeters), where the Zr atomic concentration varies in the range of 45 to 65 percent, the Ti atomic concentration varies in the range of 5 to 7.5 percent, the Al atomic concentration varies in the range of 5 to 15 percent, and the balance is a combination of Ni and Cu, where the ratio of Cu to Ni concentration is in the range of 0.5 to 2.
U.S. Pat. No. 6,521,058, entitled “High-Strength High-Toughness Amorphous Zirconium Alloy,” the disclosure of which is incorporated herein by reference in its entirety, discloses quinary Zr—Ti—Cu—Ni—Al alloys capable of forming in bulk geometries (i.e. where the thicknesses is on the order of millimeters), where the Ti atomic concentration is up to 7 percent, the combined atomic concentration of Ni and Cu varies in the range of 30 to 50 percent, where the ratio of Cu to Ni concentration is at least 3, the Al atomic concentration varies in the range of 5 to 10 percent, and the balance is Zr.
U.S. Patent Publication No. 2009/0202386, entitled “Alloys, Bulk Metallic Glass, and Methods of Forming the Same,” the disclosure of which is incorporated herein by reference in its entirety, discloses quinary Zr—Ti—Cu—Ni—Al capable of forming glasses in bulk geometries (i.e. where the thicknesses is on the order of millimeters), where the combined atomic concentration of Ni and Cu varies in the range of 37 to 48 percent, where the ratio of Cu to Ni concentration is in the range of 7/3 to 97/3, the Al atomic concentration varies in the range of 3 to 14 percent, and the balance is a combination of Zr and Ti.
Xin et al. (D. W. Xin, Y. Huang, J. Shen, “Crystallization Behaviors of ZrCuNiAlTi4 Bulk Amorphous Alloy during Continuous Heating,” Rare Metals Materials and Engineering 36(7), 1181-1184 (2007)), the disclosure of which is incorporated herein by reference in its entirety, discloses one Zr—Ti—Cu—Ni—Al metallic glass-forming alloy with composition Zr56.6Cu17.3Ni12.5Al9.6Ti4 capable of forming bulk amorphous rods with diameters of up to 3 mm. The disclosure also reports that the thermal stability of the supercooled liquid (i.e. the difference between the crystallization and glass transition temperatures) at a heating rate of 20 K/min is 75.4° C.
Kun (U. Kun, “Strukturelle und Mechanische Charakterisierung von Vielkomponentigen Amorphen, Teilamorphen und Kristallinen Zirkon-Basislegierungen,” Doctoral Dissertation, Technischen Universitat Dresden, (2004)), the disclosure of which is incorporated herein by reference in its entirety, discloses Zr—Ti—Cu—Ni—Al metallic glass-forming alloys with atomic fractions of Cu, Ni, and Al fixed at 20%, 8%, and 10% respectively, an atomic fraction of Zr in the rage of 55 to 62% and atomic fraction of Ti in the range of 0 to 7%. Rods with complete absence of crystallinity were obtained only when the rod diameter was 3 mm or less, while presence of crystals was always present in larger diameter rods. The disclosure also reported that the alloys exhibit a thermal stability of the supercooled liquid (i.e. the difference between the crystallization and glass transition temperatures) evaluated at a heating rate of 40 K/min that ranges from 54 to 118° C.
The description will be more fully understood with reference to the following figures and data graphs, which are presented as various embodiments of the disclosure and should not be construed as a complete recitation of the scope of the disclosure, wherein:
The disclosure provides Zr—Ti—Cu—Ni—Al metallic glass-forming alloys and metallic glasses that have a high glass forming ability along with a high thermal stability of the supercooled liquid against crystallization.
In one embodiment, the disclosure provides a metallic glass-forming alloy or a metallic glass having a composition represented by the following formula (subscripts denote atomic percentages):
Zr(100-a-b-c-d)TiaCubNicAld EQ. (1)
In one embodiment, the disclosure provides a metallic glass-forming alloy or a metallic glass having a composition represented by the following formula (subscripts denote atomic percentages):
Zr(100-a-b-c-d)TiaCubNicAld EQ. (1)
where:
In one embodiment, the disclosure provides a metallic glass-forming alloy or a metallic glass having a composition represented by the following formula (subscripts denote atomic percentages):
Zr(100-a-b-c-d)TiaCubNicAld EQ. (1)
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 0.5 to 3.9.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 3.8.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1.5 to 3.7.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 2 to 3.6.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 2.5 to 3.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 13 to 19.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 14 to 18.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 14.5 to 17.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 15 to 17.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 10 to 17.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 12 to 17.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 13 to 16.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 13.5 to 16.
In another embodiment of the metallic glass-forming alloy or metallic glass, d ranges from 8 to 12.
In another embodiment of the metallic glass-forming alloy or metallic glass, d ranges from 8.5 to 11.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, d ranges from 8.75 to 11.25.
In another embodiment of the metallic glass-forming alloy or metallic glass, d ranges from 9 to 11.
In another embodiment of the metallic glass-forming alloy or metallic glass, d ranges from 9.25 to 10.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, the ratio b/c ranges from 0.65 to 2.
In another embodiment of the metallic glass-forming alloy or metallic glass, the ratio b/c ranges from 0.75 to 1.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, the ratio b/c ranges from 1 to 1.5.
In another embodiment, the critical plate thickness is at least 5 mm.
In another embodiment, the critical plate thickness is at least 6 mm.
In another embodiment, the critical plate thickness is at least 7 mm.
In another embodiment, the liquidus temperature of the alloy is below 850° C.
In another embodiment, the liquidus temperature of the alloy is below 845° C.
In another embodiment, the liquidus temperature of the alloy is below 840° C.
In another embodiment, the liquidus temperature of the alloy is below 835° C.
In another embodiment, the liquidus temperature of the alloy is below 830° C.
In another embodiment, the thermal stability of the supercooled liquid is at least 79° C.
In another embodiment, the thermal stability of the supercooled liquid is at least 80° C.
In another embodiment, the thermal stability of the supercooled liquid is at least 82° C.
In another embodiment, the thermal stability of the supercooled liquid is at least 85° C.
In another embodiment, the thermal stability of the supercooled liquid is at least 90° C.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 250° C. is at least 0.7 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 240° C. is at least 0.6 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 240° C. is at least 0.8 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 230° C. is at least 0.7 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 230° C. is at least 0.9 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 220° C. is at least 0.8 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a supercooling temperature of less than 220° C. is at least 1 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.4 is at least 0.7 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.38 is at least 0.6 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.38 is at least 0.8 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.36 is at least 0.7 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.36 is at least 0.9 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.34 is at least 0.8 s.
In another embodiment, the time for isothermal crystallization when the metallic glass is heated at a normalized supercooling temperature of less than 0.34 is at least 1 s.
In another embodiment, a ranges from 0.5 to 3.9, b ranges from 13 to 19, c ranges from 10 to 17.5, and d ranges from 8 to 12, wherein the critical plate thickness is at least 4 mm, and wherein the thermal stability of the supercooled liquid is at least 80° C.
In another embodiment, a ranges from 1.5 to 3.7, b ranges from 14 to 18, c ranges from 12 to 17, and d ranges from 8.5 to 11.5, wherein the critical plate thickness is at least 5 mm, and wherein the thermal stability of the supercooled liquid is at least 85° C.
In another embodiment, a ranges from 2.5 to 3.5, b ranges from 15 to 17, c ranges from 13.5 to 16, and d ranges from 9 to 11, wherein the critical plate thickness is at least 6 mm, and wherein the thermal stability of the supercooled liquid is at least 90° C.
In another embodiment, the metallic glass-forming alloy or metallic glass may also comprise at least one of Nb, Ag, Pd, Co, Fe, Sn, and Be in a combined atomic concentration of up to 2%.
The disclosure is also directed to a method of forming a metallic glass, or an article made of a metallic glass, from the metallic glass-forming alloy.
The method includes heating and melting an ingot comprising the metallic glass-forming alloy under inert atmosphere to create a molten alloy, and subsequently quenching the molten alloy fast enough to avoid crystallization of the molten alloy.
In one embodiment, prior to quenching the molten alloy is heated to at least 100° C. above the liquidus temperature of the metallic glass-forming alloy.
In another embodiment, prior to quenching the molten alloy is heated to at least 200° C. above the liquidus temperature of the metallic glass-forming alloy.
In yet another embodiment, prior to quenching the molten alloy is heated to at least 1100° C.
In yet another embodiment, prior to quenching the molten alloy is heated to at least 1200° C.
The disclosure is also directed to a method of thermoplastically shaping a metallic glass into an article, including: heating a sample of the metallic glass to a softening temperature To above the glass transition temperature Tg, of the metallic glass to create a heated sample; applying a deformational force to shape the heated sample over a time to that is shorter than the time it takes for the metallic glass to crystallize at To, and cooling the heated sample to a temperature below Tg to form an article.
In one embodiment, To is higher than Tg and lower the liquidus temperature of the metallic glass-forming alloy.
In another embodiment, To is greater than Tg and lower than Tx.
In another embodiment, To is higher than Tx and lower than the solidus temperature of the metallic glass-forming alloy.
In another embodiment, To is in the range of 500 to 800° C.
In another embodiment, To is in the range of 525 to 700° C.
In another embodiment, To is in the range of 550 to 650° C.
In another embodiment, To is such that the supercooling temperature is in the range of 190 to 260° C.
In another embodiment, To is such that the supercooling temperature is in the range of 200 to 250° C.
In another embodiment, To is such that the supercooling temperature is in the range of 210 to 240° C.
In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.3 to 0.4.
In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.31 to 0.39.
In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.32 to 0.38.
In another embodiment, the viscosity of the sample at To is less than 105 Pa-s.
In another embodiment, the viscosity of the sample at To is in the range of 100 to 105 Pa-s.
In another embodiment, the viscosity of the sample at To is in the range of 101 to 104 Pa-s.
In another embodiment, heating of the sample of the metallic glass-forming alloy is performed by conduction to a hot surface.
In another embodiment, heating of the sample of the metallic glass-forming alloy is performed by inductive heating.
In another embodiment, heating of the sample of the metallic glass-forming alloy is performed by ohmic heating.
In another embodiment, the ohmic heating is performed by the discharge of at least one capacitor.
The disclosure is also directed to a metallic glass-forming alloy or a metallic glass having compositions selected from a group consisting of: Zr56.5Ti1Cu17.9Ni14.6Al10, Zr55.5Ti2Cu17.9Ni14.6Al10, Zr55Ti2.5Cu17.9Ni14.6Al10, Zr54.5Ti3Cu17.9Ni14.6Al10, Zr54Ti3.5Cu17.9Ni14.6Al10, Zr55.5Ti3Cu17.9Ni14.6Al9, Zr53.5Ti3Cu17.9Ni14.6Al11, Zr56.5Ti3Cu17.9Ni12.6Al10, Zr56.5Ti3Cu17.9Ni16.6Al10, Zr58.5Ti3Cu13.9Ni14.6Al10, Zr57.5Ti3Cu14.9Ni14.6Al10, Zr56.5Ti3Cu15.9Ni14.6Al10, Zr55.5Ti3Cu16.9Ni14.6Al10, and Zr53.5Ti3Cu18.9Ni14.6Al10.
The disclosure may be understood by reference to the following detailed description, taken in conjunction with the drawings as described below. It is noted that, for purposes of illustrative clarity, certain elements in various drawings may not be drawn to scale.
In the disclosure, the glass-forming ability of each alloy is quantified by the “critical plate thickness,” defined as the largest plate thickness in which the amorphous phase can be formed when processed by a method of casting the molten alloy in a copper mold having a prismatic cavity, where at least one dimension of the rectangular cavity is lower than 50% of at least one other dimension of the rectangular cavity.
A “critical cooling rate,” which is defined as the cooling rate required to avoid crystallization and form the amorphous phase of the metallic glass-forming alloy (i.e. the metallic glass), determines the critical plate thickness. The lower the critical cooling rate of a metallic glass-forming alloy, the larger its critical plate thickness. The critical cooling rate Rc in K/s and critical plate thickness tc in mm are related via the following approximate empirical formula:
Rc=1000/tc2 Eq. (2)
According to Eq. (2), the critical cooling rate for a metallic glass-forming alloy having a critical casting thickness of about 1 mm is about 103 K/s.
Generally, three categories are known in the art for identifying the ability of an alloy to form a metallic glass (i.e. to bypass the stable crystal phase and form an amorphous phase). Alloys having critical cooling rates in excess of 1012 K/s are typically referred to as non-glass formers, as it is physically impossible to achieve such cooling rates over a meaningful thickness. Alloys having critical cooling rates in the range of 105 to 1012 K/s are typically referred to as marginal glass formers, as they are able to form metallic glass foils or ribbons with thicknesses ranging from 1 to 100 micrometers according to EQ. (2). Metal alloys having critical cooling rates on the order of 103 or less, and as low as 1 or 0.1 K/s, are typically referred to as bulk glass formers, as they are able to form metallic glass plates with thicknesses ranging from 1 millimeter to several centimeters. The glass-forming ability of a metallic alloy is, to a very large extent, dependent on the composition of the metallic glass-forming alloy. The compositional ranges for alloys that are marginal glass formers are considerably broader than those which are bulk glass formers.
Often in the art, a measure of glass forming ability of an alloy is reported as the critical rod diameter instead of the critical plate thickness. Due to its symmetry, the diameter of a rod for which a certain cooling rate is achieved at its centerline is about twice the thickness of a plate for which the same cooling rate is achieved at its centerline. Hence, the critical rod diameter to achieve a critical cooling rate is about twice the critical plate thickness to achieve the same critical cooling rate. Therefore, a critical rod diameter can be approximately converted to a critical plate thickness by dividing by 2.
In the disclosure, the thermal stability of the supercooled liquid ΔTx is defined as the difference between the crystallization temperature Tx and the glass transition temperature Tg of the metallic glass, ΔTx=Tx−Tg, measured by calorimetry at a heating rate of 20 K/min.
The thermal stability of the supercooled liquid ΔTx is a property defining the ability of the metallic glass to be shaped “thermoplastically” in the supercooled liquid region, i.e. to be shaped by heating the metallic glass to a softening temperature To above the glass transition temperature Tg, applying a deformational force to shape the metallic glass over a time to that is shorter than the time it takes for the softened metallic glass to crystallize at To, and cooling the metallic glass to a temperature below Tg. The higher the thermal stability of the supercooled liquid ΔTx, the longer the available time to, which allows for application of the deformational force for longer periods and thus enables larger shaping strains. Also, the higher the thermal stability of the supercooled liquid ΔTx, the higher the softening temperature To that the metallic glass can be heated, which would result in lower viscosities and thus allow larger shaping strains.
In the disclosure, the supercooling temperature is defined as the difference between the softening temperature To and the glass transition temperature Tg, i.e. To−Tg, expressed in units of either ° C. or K. Also, the normalized supercooling temperature is defined as the difference between the softening temperature To and the glass transition temperature Tg, divided by the glass transition temperature Tg, i.e. (To−Tg)/Tg, expressed in units of K/K.
In some embodiments, To is higher than Tg and lower than the liquidus temperature of the metallic glass-forming alloy. In one embodiment, To is greater than Tg and lower than Tx. In another embodiment, To is higher than Tx and lower than the solidus temperature of the metallic glass-forming alloy. The liquidus temperature is the temperature above which a metallic glass-forming alloy is an equilibrium liquid. The solidus temperature is the temperature above which the crystalline state of the metallic glass-forming alloy begins to melt.
In another embodiment, To is in the range of 500 to 800° C. In another embodiment, To is in the range of 525 to 700° C. In another embodiment, To is in the range of 550 to 650° C. In another embodiment, To is such that the supercooling temperature is in the range of 190 to 260° C. In another embodiment, To is such that the supercooling temperature is in the range of 200 to 250° C. In another embodiment, To is such that the supercooling temperature is in the range of 210 to 240° C. In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.3 to 0.4. In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.31 to 0.39. In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.32 to 0.38. In some embodiments, the viscosity at To is less than 105 Pa-s. In one embodiment, the viscosity at To is in the range of 100 to 105 Pa-s. In another embodiment, the viscosity at To is in the range of 101 to 104 Pa-s.
In addition to exhibiting large thermal stability of the supercooled liquid ΔTx, the metallic glasses can be capable of being formed in bulk (i.e. millimeter-thick) dimensions in order to enable “thermoplastic” shaping of bulk 3-dimensional articles. That is, metallic glasses having both a high glass-forming ability as well as a large ΔTx would be suitable for “thermoplastic” shaping of bulk articles. Discovering compositional regions where the metallic glass demonstrates a high glass forming ability is unpredictable. Discovering compositional regions where the metallic glass demonstrates a large ΔTx is equally unpredictable. Discovering compositional regions where the metallic glass demonstrates both a high glass forming ability and a large ΔTx is even more unpredictable than both cases above, because metallic glasses that demonstrate a high glass forming ability do not necessarily demonstrate a large ΔTx, and vice versa. In the context of this disclosure, a critical plate thickness of at least 4 mm and a ΔTx of at least 78° C. may be sufficient to enable “thermoplastic” shaping of bulk 3-dimensional articles.
In this disclosure, compositional regions in the Zr—Ti—Cu—Ni—Al alloys are disclosed where the metallic glass-forming alloys demonstrate a high glass forming ability while the metallic glasses formed from the alloys demonstrate a large ΔTx. In embodiments of the disclosure, the metallic glass-forming alloys demonstrate a critical plate thickness of at least 4 mm, while the metallic glasses formed from the alloys demonstrate a ΔTx of at least 78° C. In some embodiments, the critical plate thickness is at least 5 mm, in other embodiments the critical plate thickness is at least 6 mm, while in other embodiments the critical plate thickness is at least 7 mm. In some embodiments, the thermal stability of the supercooled liquid is at least 79° C., in other embodiments at least 80° C., in other embodiments at least 82° C., in other embodiments at least 85° C., while in other embodiments at least 90° C.
The disclosure is also directed to methods of forming a metallic glass, or an article made of a metallic glass, from the metallic glass-forming alloy. In various embodiments, a metallic glass is formed by heating and melting an alloy ingot under inert atmosphere to create a molten alloy, and subsequently quenching the molten alloy fast enough to avoid crystallization of the molten alloy. In one embodiment, prior to cooling the molten alloy is heated to at least 100° C. above the liquidus temperature of the metallic glass-forming alloy. In another embodiment, prior to quenching the molten alloy is heated to at least 200° C. above the liquidus temperature of the metallic glass-forming alloy. In another embodiment, prior to quenching the molten alloy is heated to at least 1100° C. In yet another embodiment, prior to quenching the molten alloy is heated to at least 1200° C. In one embodiment, the alloy ingot is heated and melted using a plasma arc. In another embodiment, the alloy ingot is heated and melted using an induction coil. In some embodiments, the alloy ingot is heated and melted over a water-cooled hearth, or within a water-cooled crucible. In one embodiment, the hearth or crucible is made of copper. In some embodiments, the inert atmosphere comprises argon gas. In some embodiments, quenching of the molten alloy is performed by injecting or pouring the molten alloy into a metal mold. In some embodiments, the mold can be made of copper, brass, or steel, among other materials. In some embodiments, injection of the molten alloy is performed by a pneumatic drive, a hydraulic drive, an electric drive, or a magnetic drive. In some embodiments, pouring the molten alloy into a metal mold is performed by tilting a tandish containing the molten alloy.
The disclosure is also directed to methods of thermoplastically shaping a metallic glass into an article. In some embodiments, heating of the metallic glass is performed by conduction to a hot surface. In other embodiments, heating of the metallic glass to a softening temperature To above the glass transition temperature Tg is performed by inductive heating. In yet other embodiments, heating of the metallic glass to a softening temperature To above the glass transition temperature Tg is performed by ohmic heating. In one embodiment, the ohmic heating is performed by the discharge of at least one capacitor. In some embodiments, the application of the deformational force to thermoplastically shape the softened metallic glass in the supercooled liquid region is performed by a pneumatic drive, a hydraulic drive, an electric drive, or a magnetic drive.
Description of the Metallic Glass Forming Region
In various embodiments, the disclosure provides Zr—Ti—Cu—Ni—Al alloys capable of forming metallic glasses. The alloys demonstrate a critical plate thickness of at least 4 mm, and the metallic glasses demonstrate a thermal stability of the supercooled liquid of at least 78° C.
Specifically, the disclosure provides Zr—Ti—Cu—Ni—Al metallic glass-forming alloys and metallic glasses where Ti ranges over a relatively narrow range, over which the alloys demonstrate a critical plate thickness of at least 4 mm and 6 mm or higher, while the metallic glasses formed from the alloys demonstrate a thermal stability of the supercooled liquid of at least 78° C. and 96° C. or higher. In some embodiments, the Ti range is from 0.5 to less than 4 atomic percent, in other embodiments the Ti range is from 0.5 to 3.9 atomic percent, in other embodiments the Ti range is from 1 to 3.8 atomic percent, in other embodiments the Ti range is from 1.5 to 3.7 atomic percent, in other embodiments the Ti range is from 2 to 3.6 atomic percent, while in other embodiments the Ti range is from 2.5 to 3.5 atomic percent.
In one embodiment, the disclosure provides an alloy capable of forming a metallic glass having a composition represented by the following formula (subscripts denote atomic percentages):
Zr(100-a-b-c-d)TiaCubNicAld EQ. (1)
In another embodiment, a ranges from 0.5 to 3.9, b ranges from 13 to 19, c ranges from 10 to 17.5, and d ranges from 8 to 12, wherein the critical plate thickness is at least 4 mm, and wherein the thermal stability of the supercooled liquid is at least 80° C.
In another embodiment, a ranges from 1.5 to 3.7, b ranges from 14 to 18, c ranges from 12 to 17, and d ranges from 8.5 to 11.5, wherein the critical plate thickness is at least 5 mm, and wherein the thermal stability of the supercooled liquid is at least 85° C.
In another embodiment, a ranges from 2.5 to 3.5, b ranges from 15 to 17, c ranges from 13.5 to 16, and d ranges from 9 to 11, wherein the critical plate thickness is at least 6 mm, and wherein the thermal stability of the supercooled liquid is at least 90° C.
Specific embodiments of metallic glasses formed of alloys having compositions according to the formula Zr57.5-xTixCu17.9Ni14.6Al10, where the concentration of Ti in the alloys ranges from 1 to less than 4 atomic percent, demonstrate a critical plate thickness of at least 4 mm, while the metallic glasses formed from the alloys demonstrate a thermal stability of the supercooled liquid of at least 78° C.
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Zr57.5-xTixCu17.9Ni14.6Al10 are presented in Table 1. In these alloys, Zr is substituted by Ti, where the atomic fraction of Ti varies from 1 to 5 percent, the atomic fraction of Zr varies from 52.5 to 56.5 percent, while the atomic fractions of Cu, Ni, and Al are fixed at 17.9, 14.6, and 10, respectively.
As shown in Table 1 and
The critical plate thicknesses of the example alloys according to the composition formula Zr57.5-xTixCu17.9Ni14.6Al10 are listed in Table 2. As shown in Table 2, substituting Zr by Ti according to Zr57.5-xTixCu17.9Ni14.6Al10 results in varying glass forming ability. Specifically, the critical plate thickness increases from 4 mm for the metallic glass-forming alloy containing 1 atomic percent Ti (Example 1), reaches the highest value of 5 mm for the metallic glass-forming alloy containing 3 atomic percent Ti (Example 4), and decreases back to 4 mm for the metallic glass-forming alloy containing 5 atomic percent Ti (Example 7)
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Zr64.5-xTi3Cu17.9Ni14.6Alx are presented in Table 3. In these metallic glass-forming alloys, Zr is substituted by Al, where the atomic fraction of Al varies from 9 to 11 percent, the atomic fraction of Zr varies from 53.5 to 55.5 percent, while the atomic fractions of Ti, Cu, and Ni are fixed at 3, 17.9, and 14.6, respectively.
As shown in Table 3 and
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Zr69.1-xTi3Cu17.9NixAl10 are presented in Table 4. In these alloys, Zr is substituted by Ni, where the atomic fraction of Ni varies from 12.6 to 16.6 percent, the atomic fraction of Zr varies from 52.5 to 56.5 percent, while the atomic fractions of Ti, Cu, and Al are fixed at 3, 17.9, and 10, respectively.
As shown in Table 4 and
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Zr72.4-xTi3CuxNi14.6Al10 are presented in Table 5. In these metallic glass-forming alloys, Zr is substituted by Cu, the atomic fraction of Cu varies from 13.9 to 18.9 percent, the atomic fraction of Zr varies from 53.5 to 58.5 percent, while the atomic fractions of Ti, Ni, and Al are fixed at 3, 14.6, and 10, respectively.
As shown in Table 5 and
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Zr71.1-xTi3Cu15.9NixAl10 are presented in Table 6. In these metallic glass-forming alloys, Zr is substituted by Ni, the atomic fraction of Ni varies from 10.6 to 14.6 percent, the atomic fraction of Zr varies from 56.5 to 60.5 percent, while the atomic fractions of Ti, Cu, and Al are fixed at 3, 15.9, and 10, respectively. The glass transition temperature Tg and crystallization temperature Tx of metallic glasses are listed in Table 6, along with the difference between crystallization and glass-transition temperatures ΔTx=Tx−Tg.
The critical plate thicknesses of the example metallic glass-forming alloys according to the composition formula Zr71.1-xTi3Cu15.9NixAl10 are listed in Table 7. As shown in Table 7, substituting Zr by Ni according to Zr71.1-xTi3Cu15.9NixAl10 results in a fairly constant glass forming ability. Specifically, the critical plate thickness of the metallic glass-forming alloy is 6 mm when the atomic concentration of Ni is between 12.6 and 14.6 (Example 14 and 18), while the critical plate thickness of the metallic glass-forming alloy slightly increases to 7 mm when the atomic concentration of Ni is 10.6 (Example 19).
Other embodiments of metallic glasses formed of glass-forming alloys according to the disclosure are presented in Table 8. The glass transition temperature Tg and crystallization temperature Tx of metallic glasses are listed in Table 6, along with the difference between the crystallization and glass-transition temperatures, ΔTx=Tx−Tg.
As shown in Tables 1-5, and
The higher glass forming ability demonstrated by the metallic glass-forming alloys of the disclosure compared to known alloys may be attributed to a significantly lower liquidus temperature of the present metallic glass-forming alloys.
As seen in
Isothermal Crystallization Kinetics
To demonstrate the ability of the disclosed metallic glasses to resist crystallization at high softening temperatures deep into the supercooled liquid region, isothermal crystallization experiments were performed. Such experiments enable determination of the time for crystallization, to, at a given softening temperature, To, where the metallic glass is heated to. Sampling to at various To enables construction of a TTT (Time-Temperature-Transformation diagram). These experiments were performed on two metallic glasses: Zr52.5Ti5Cu17.9Ni14.6Al10 (Example 7) which is a known metallic glass, and Zr60.5Ti3Cu15.9Ni10.6Al10 (Example 19), which is according to embodiments of the disclosure.
The heating experiments to heat the metallic glass in millisecond time scales to a softening temperature To that is uniform across the sample and constant with time were performed by ohmic heating via capacitive discharge. Attaining a uniform and constant temperature is necessary in order to alloy the metallic glass to crystallize isothermally by homogeneous nucleation. A high-speed infrared camera was employed to ensure that the temperature remained uniform through the sample during the isothermal time interval, and that the crystallization was initiated by homogeneous nucleation. Multiple experiments were performed for metallic glasses Zr52.5Ti5Cu17.9Ni14.6Al10 and Zr60.5Ti3Cu15.9Ni10.6Al10, where various capacitive energies were used for each metallic glass to reach various softening temperatures To.
A plot of an example heating curve for metallic glass Zr52.5Ti5Cu17.9Ni14.6Al10 is presented
To compare the resistance of each metallic glass against crystallization in the supercooled liquid region, a temperature scale should be used that express the softening temperature To in relation to the glass transition temperature Tg, such that the thermal stability of the supercooled liquid is quantified.
In one embodiment, a temperature scale quantifying the thermal stability of the supercooled liquid is represented by the supercooling temperature, defined as the difference between the softening temperature To and the glass transition temperature Tg, i.e. To−Tg, expressed in units of either ° C. or K. The supercooling temperatures for metallic glasses Zr52.5Ti5Cu17.9Ni14.6Al10 (Example 7) and Zr60.5Ti3Cu15.9Ni10.6Al10 (Example 19) are listed in Tables 10 and 11, respectively. The TTT diagrams, where the temperature axis is represented by the supercooling temperature for metallic glasses Zr52.5Ti5Cu17.9Ni14.6Al10 (Example 7) and Zr60.5Ti3Cu15.9Ni10.6Al10 (Example 19), are plotted in
Therefore, metallic glasses according to some embodiments of the disclosure, when heated at supercooling temperatures below 250° C., can resist isothermal crystallization for at least 0.5 s. Metallic glasses according to other embodiments of the disclosure, when heated at supercooling temperatures below 250° C., can resist isothermal crystallization for at least 0.7 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 240° C., can resist isothermal crystallization for at least 0.6 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 240° C., can resist isothermal crystallization for at least 0.8 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 230° C., can resist isothermal crystallization for at least 0.7 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 230° C., can resist isothermal crystallization for at least 0.9 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 220° C., can resist isothermal crystallization for at least 0.8 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at supercooling temperatures below 220° C., can resist isothermal crystallization for at least 1 s.
In another embodiment, a temperature scale quantifying the supercooled liquid stability is represented by the normalized supercooling temperature, defined as the difference between the softening temperature To and the glass transition temperature Tg, divided by the glass transition temperature Tg, i.e. (To−Tg)/Tg, expressed in units of K/K. The normalized supercooling temperatures for metallic glasses Zr52.5Ti5Cu17.9Ni14.6Al10 (Example 7) and Zr60.5Ti3Cu15.9Ni10.6Al10 (Example 19) are listed in Tables 10 and 11, respectively. Also the TTT diagrams where the temperature axis is represented by the normalized supercooling temperature for metallic glasses Zr52.5Ti5Cu17.9Ni14.6Al10 (Example 7) and Zr60.5Ti3Cu15.9Ni10.6Al10 (Example 19) are plotted in
Therefore, metallic glasses according to some embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.4, can resist isothermal crystallization for at least 0.5 s. Metallic glasses according to other embodiments of the disclosure, when heated at supercooling temperatures below 0.4, can resist isothermal crystallization for at least 0.7 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.38, can resist isothermal crystallization for at least 0.6 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.38, can resist isothermal crystallization for at least 0.8 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.36, can resist isothermal crystallization for at least 0.7 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.36, can resist isothermal crystallization for at least 0.9 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.34, can resist isothermal crystallization for at least 0.8 s. Metallic glasses according to yet other embodiments of the disclosure, when heated at normalized supercooling temperatures below 0.34, can resist isothermal crystallization for at least 1 s.
Methods of Processing Alloy Ingots of Sample Metallic Glass-Forming Alloys
A particular method for producing alloy ingots for the sample metallic glass-forming alloys involves arc melting of the appropriate amounts of elemental constituents over a water-cooled copper hearth under a titanium-gettered argon atmosphere. The purity levels of the constituent elements were as follows: Zr 99.9% (crystal bar), Ti 99.9% (crystal bar), Cu 99.995%, Ni 99.995%, and Al 99.999%. The argon atmosphere was created by first establishing vacuum at 1.5×10−4 mbar, followed by a purge of ultra-high purity argon gas (99.999% purity) to establish a pressure of 800 mbar.
Methods of Processing Sample Metallic Glass Plates
A particular method for producing metallic glass plates from the metallic glass-forming alloy ingots for the sample metallic glass-forming alloys involves melting the alloy ingots over a water-cooled copper hearth under a titanium-gettered argon atmosphere to form an alloy melt, heating the alloy melt to a temperature of at least 1200° C., and subsequently pouring the alloy melt into a copper mold. Copper molds having a prismatic cavity with length of 55 mm, width of 22 mm, and varying thickness were used. The argon atmosphere was created by first establishing vacuum at 1.5×10−4 mbar, followed by a purge of ultra-high purity argon gas (99.999% purity) to establish a pressure of 800 mbar.
Test Methodology for Differential Scanning Calorimetry
Differential scanning calorimetry was performed on sample metallic glasses at a scan rate of 20 K/min to determine the glass-transition, crystallization, solidus, and liquidus temperatures of sample metallic glasses.
Method of Producing Metallic Glass Rods for Evaluating Isothermal Crystallization Kinetics
Metallic glass rods having 7 mm in diameter and about 100 mm in length were produced from the alloy ingots by the method of counter-gravity casting, where molten liquid contained in fused silica crucible is injected upwards (against gravity) into a mold using gas pressure. An inert atmosphere was created in a melt chamber by first applying vacuum at 5×10−2 mbar and subsequently following several purges with argon, an argon atmosphere was established having a pressure of −3 to −5 in-Hg. The ingot was heated inductively first to 1200° C. to create a homogeneous high temperature melt and then allowed to cool back to 1100° C., and were subsequently urged upwards using an argon pressure of 2-3 psi through a fused silica straw of 7 mm inner diameter into a tool steel (H-13) mold having a rod-shaped cavity 7 mm in diameter and 100 mm in length. The melt was rapidly cooled in the mold to produce a quenched metallic glass rod having 7 mm in diameter and 100 mm in length. Multiple metallic glass rods were produced this way. The rods were sectioned to form shorter rods of 35-40 mm in length. The amorphicity of each rod was verified by x-ray diffraction. The rods were machined on a lathe to reduce their diameters from 7 mm to 5 mm, in order to eliminate any entrained pores near the surface that would cause localized heating and prematurely catalyze crystallization.
Method of Measuring the Sample Heating Response in Evaluating Crystallization Kinetics
Metallic glass rods having 5 mm in diameter and length ranging between 35 and 40 mm produced as described above were clamped on each end between two copper collets with exposed length of approximately 35 mm. The copper plates were clamped in a vise and attached to leads of a capacitive discharge circuit. The capacitive discharge circuit has been disclosed in conjunction with a rapid capacitive discharging forming (RCDF) apparatus, such as in the following patents or patent applications: U.S. Pat. No. 8,613,813, entitled “Forming of metallic glass by rapid capacitor discharge;” U.S. Pat. No. 8,613,814, entitled “Forming of metallic glass by rapid capacitor discharge forging”; U.S. Pat. No. 8,613,815, entitled “Sheet forming of metallic glass by rapid capacitor discharge;” U.S. Pat. No. 8,613,816, entitled “Forming of ferromagnetic metallic glass by rapid capacitor discharge;” U.S. Pat. No. 9,297,058, entitled “Injection molding of metallic glass by rapid capacitor discharge;” and U.S. patent application Ser. No. 15/406,436, entitled “Feedback-assisted rapid discharge heating and forming of metallic glasses,” each of which is incorporated by reference in its entirety.
A high-speed infrared pyrometer with a response time of 6 μs and an Indium-Gallium-Arsenide sensor with a spectral range of 1.58-2.2 μm were used to measure the temperature at the midpoint of each rod. A high speed infrared imaging camera (FLIR Corp., SC2500) with a spectral band from 0.9 to 1.7 mm outfitted with a bandpass filter allowing wavelengths from 1.5 to 1.9 mm was employed to record the evolution of the temperature distribution during heating, and to ensure that crystallization was initiated homogeneously from the midpoint of the rod. A Rogowski coil current sensor and voltage probe were used to measure the current and voltage, respectively, of the capacitive discharge pulse. Data from these sources were collected with an oscilloscope. Current and voltage data were used to verify that there were no anomalies in the shape of the current pulse.
Having described several embodiments, it will be recognized by those skilled in the art that various modifications, alternative constructions, and equivalents may be used without departing from the spirit of the invention. Additionally, a number of well-known processes and elements have not been described in order to avoid unnecessarily obscuring the present invention. Accordingly, the above description should not be taken as limiting the scope of the invention.
Those skilled in the art will appreciate that the presently disclosed embodiments teach by way of example and not by limitation. Therefore, the matter contained in the above description or shown in the accompanying drawings should be interpreted as illustrative and not in a limiting sense. The following claims are intended to cover all generic and specific features described herein, as well as all statements of the scope of the present method and system, which, as a matter of language, might be said to fall therebetween.
This patent application claims the benefit of U.S. Patent Application No. 62/299,365, entitled “ZIRCONIUM-TITANIUM-COPPER-NICKEL-ALUMINUM GLASSES WITH HIGH GLASS FORMING ABILITY AND HIGH THERMAL STABILITY,” filed on Feb. 24, 2016 under 35 U.S.C. § 119(e), which is incorporated herein by reference in its entirety.
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