Patent Grant
11371108
The disclosure is directed to Fe—Cr—Mo—Ni—P—C—B metallic glasses having a high glass forming ability and a high thermal stability of the supercooled liquid against crystallization.
U.S. Pat. Nos. 8,529,712 and 8,911,572 entitled “Tough Iron-Based Bulk Metallic Glass Alloys,” the disclosures of which is incorporated herein by reference in their entirety, disclose Fe-based glass forming alloys comprising at least P, C, and B demonstrating a critical rod diameter of at least 2 mm and a shear modulus of less than 60 GPa, where the Fe atomic concentration is at least 60 percent, the P atomic concentration varies in the range of 5 to 17.5 percent, the C atomic concentration varies in the range of 3 to 6.5 percent, and the B atomic concentration varies in the range of 1 to 3.5 percent. The patents also disclose that the Fe-based alloys may optionally comprise Mo in an atomic concentration varying in the range of 2 to 8 percent, Cr in an atomic concentration varying in the range of 1 to 7 percent, and Ni in an atomic concentration varying in the range of 3 to 7 percent. The patents present several examples of amorphous Fe—P—C—B alloys that comprise Mo, Cr, and Ni demonstrating a critical rod diameter of up to 6 mm and a thermal stability of the supercooled liquid (i.e. a difference between the crystallization and glass transition temperatures at a heating rate of 20 K/min) of under 40° 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 Fe—Cr—Ni—Mo—P—C—B 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):
Fe(100-a-b-c-d-e-f)CraNibMocPdCeBf EQ. (1)
In another embodiment of the metallic glass-forming alloy or metallic glass, a is up to 9, b ranges from 4 to 12, c ranges from 3 to 6.5, d+e+f ranges from 21.5 to 23.5, e ranges from 5.25 to 7.5, f ranges from 1.5 to 8.5, wherein the metallic glass-forming alloy has a critical rod diameter of at least 4 mm, and wherein the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 47.5° C.
In another embodiment of the metallic glass-forming alloy or metallic glass, a is up to 8, b ranges from 4.5 to 10, c ranges from 3.5 to 5.5, d+e+f ranges from 21.5 to 23, e ranges from 5.5 to 7, f ranges from 2 to 7.5, wherein the metallic glass-forming alloy has a critical rod diameter of at least 5 mm, and wherein the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 50° C.
In another embodiment of the metallic glass, a is less than 3.5, and wherein the critical bending diameter of the metallic glass is at least 0.5 mm.
In another embodiment of the metallic glass, a is less than 2.5, and wherein the critical bending diameter of the metallic glass is at least 0.6 mm.
In another embodiment of the metallic glass, a is less than 1.75, and wherein the critical bending diameter of the metallic glass is at least 0.7 mm.
In another embodiment of the metallic glass, a is less than 1.25, and wherein the critical bending diameter of the metallic glass is at least 0.8 mm.
In another embodiment of the metallic glass, c ranges from 2 to less than 6.5, and wherein the critical bending diameter of the metallic glass is at least 0.6 mm.
In another embodiment of the metallic glass, c ranges from 2 to less than 5.5, and wherein the critical bending diameter of the metallic glass is at least 0.7 mm.
In another embodiment of the metallic glass, c ranges from 2 to less than 4.25, and wherein the critical bending diameter of the metallic glass is at least 0.8 mm.
In another embodiment of the metallic glass, d+e+f ranges from 21.25 to less than 23.5, and wherein the critical bending diameter of the metallic glass is at least 0.6 mm.
In another embodiment of the metallic glass, d+e+f ranges from 21.25 to less than 22.75, and wherein the critical bending diameter of the metallic glass is at least 0.7 mm.
In another embodiment of the metallic glass, e ranges from greater than 5.25 to 8, and wherein the critical bending diameter of the metallic glass is at least 0.8 mm.
In another embodiment of the metallic glass, e ranges from greater than 6.75 to 8, and wherein the critical bending diameter of the metallic glass is at least 0.9 mm.
In another embodiment of the metallic glass, f ranges from 1 to less than 5, and wherein the critical bending diameter of the metallic glass is at least 0.5 mm.
In another embodiment of the metallic glass, f ranges from 1 to less than 4.5, and wherein the critical bending diameter of the metallic glass is at least 0.6 mm.
In another embodiment of the metallic glass, f ranges from 1 to less than 3, and wherein the critical bending diameter of the metallic glass is at least 0.7 mm.
In another embodiment of the metallic glass, f ranges from 1 to less than 2.5, and wherein the critical bending diameter of the metallic glass is at least 0.8 mm.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 6.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 5.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 4.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 3.
In another embodiment of the metallic glass-forming alloy or metallic glass, a ranges from 1 to 2.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 4 to 11.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 5 to 10.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 6 to 10.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 7 to 10.
In another embodiment of the metallic glass-forming alloy or metallic glass, b ranges from 8 to 10.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 2.5 to 6.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 3 to 6.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 3.5 to 5.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 3.75 to 5.25.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 3.75 to 5.
In another embodiment of the metallic glass-forming alloy or metallic glass, c ranges from 3.75 to 4.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, d+e+f ranges from 21.25 to 23.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, d+e+f ranges from 21.5 to 23.
In another embodiment of the metallic glass-forming alloy or metallic glass, d+e+f ranges from 21.75 to 22.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5 to 7.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5.25 to 7.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5.25 to 7.25.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5.25 to 7.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5.25 to 6.75.
In another embodiment of the metallic glass-forming alloy or metallic glass, e ranges from 5.5 to 6.5.
In another embodiment of the metallic glass-forming alloy or metallic glass, f ranges from 2 to 5.
In another embodiment of the metallic glass-forming alloy or metallic glass, f ranges from 2 to 4.
In another embodiment of the metallic glass-forming alloy or metallic glass, f ranges from 2 to 3.
In another embodiment, the metallic glass-forming alloy has a critical rod diameter of at least 4 mm.
In another embodiment, the metallic glass-forming alloy has a critical rod diameter of at least 5 mm.
In another embodiment, the metallic glass-forming alloy has a critical rod diameter of at least 6 mm.
In another embodiment, the metallic glass-forming alloy has a critical rod diameter of at least 7 mm.
In another embodiment, the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 51° C.
In another embodiment, the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 52° C.
In another embodiment, the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 53° C.
In another embodiment, the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 54° C.
In another embodiment, the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 55° C.
In another embodiment, the critical bending diameter of the metallic glass is at least 0.5 mm.
In another embodiment, the critical bending diameter of the metallic glass is at least 0.6 mm.
In another embodiment, the critical bending diameter of the metallic glass is at least 0.7 mm.
In another embodiment, the critical bending diameter of the metallic glass is at least 0.8 mm.
In another embodiment, up to 5 atomic percent of Fe is substituted by Co, Ru, Mn, or a combination thereof.
In another embodiment, up to 2 atomic percent of Ni is substituted by Pd, Pt, or a combination thereof.
In another embodiment, up to 1 atomic percent of Mo is substituted by Nb, Ta, V, W, or a combination thereof.
In another embodiment, up to 2 atomic percent of P is substituted by Si.
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 1200° C.
In yet another embodiment, prior to quenching the molten alloy is heated to at least 1300° C.
The disclosure is also directed to a method of thermoplastically shaping a metallic glass into an article, including:
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 T.
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 550 to 850° C.
In another embodiment, To is in the range of 575 to 750° C.
In another embodiment, To is in the range of 600 to 700° C.
In another embodiment, To is such that the supercooling temperature is in the range of 200 to 300° C.
In another embodiment, To is such that the supercooling temperature is in the range of 225 to 275° C.
In another embodiment, To is such that the supercooling temperature is in the range of 235 to 265° C.
In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.25 to 0.5.
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 0.325 to 0.375.
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 10° 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: Fe67Ni7Mo4P13.5C6B2.5, Fe67Ni7Mo4P13C6.5B2.5, Fe67Ni7Mo4P12.5C7B2.5, Fe67Ni7Mo4P14C6B2, Fe67Ni7Mo4P13C6B3, Fe67Ni7Mo4P12.5C6B3.5, Fe67Ni7Mo4P12C6B4, Fe66.5Ni7Mo4.5P13.5C6B2.5, Fe66Ni7Mo5P13.5C6B2.5, Fe69Ni5Mo4P13.5C6B2.5, Fe65Ni9Mo4P13.5C6B2.5, Fe64Ni9Cr1Mo4P13.5C6B2.5, Fe63.5Ni9Cr1.5Mo4P13.5C6B2.5, Fe63Ni9Cr2Mo4P13.5C6B2.5, Fe62Ni9Cr3Mo4P13.5C6B2.5, Fe63.7Ni9.03Cr1.51Mo4.01P13.35C5.93B2.47, Fe63.1Ni8.94Cr1.49Mo3.97P13.81C6.13B2.56, and Fe62.69Ni8.88Cr1.48Mo3.95P14.12C6.27B2.61.
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 an alloy is quantified by the “critical rod diameter,” defined as maximum rod diameter in which the amorphous phase can be formed when processed by a method of water quenching a quartz tube with a 0.5 mm thick wall containing the molten alloy.
The “critical cooling rate”, which is defined as the cooling rate to avoid crystallization and form the amorphous phase of the alloy (i.e. a metallic glass), determines the “critical rod diameter”. The lower the critical cooling rate of an alloy, the larger its critical rod diameter. The critical cooling rate Rc in K/s and critical rod diameter d, in mm are related via the following approximate empirical formula:
Rc=1000/dc2 Eq. (2)
For example, according to Eq. (2), the critical cooling rate for an alloy having a critical rod diameter of about 3 mm is about 102 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 very difficult to achieve such cooling rates and form the amorphous phase over a meaningful cross-section thickness (i.e. at least 1 micrometer). 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 glass over thicknesses ranging from 1 to 100 micrometers according to Eq. (2). 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 glass over thicknesses ranging from 1 millimeter to several centimeters. The glass-forming ability of an alloy (and by extension its critical cooling rate and critical rod diameter) is, to a very large extent, dependent on the composition of the alloy. The compositional ranges for alloys capable of forming marginal glass formers are considerably broader than those for forming bulk glass formers.
Often in the art, a measure of glass forming ability of an alloy is reported as the critical plate thickness instead of the critical rod diameter. Due to its symmetry, the diameter of a rod to achieve a certain cooling rate at the centerline is about twice the thickness of a plate for achieving the same cooling rate at the centerline. Hence, the critical plate thickness to achieve a critical cooling rate is about half the critical rod diameter to achieve the same critical cooling rate. Therefore, a critical plate thickness can be approximately converted to a critical rod diameter by multiplying 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 T. 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 550 to 850° C. In another embodiment, To is in the range of 575 to 750° C. In yet another embodiment, To is in the range of 600 to 700° C. In another embodiment, To is such that the supercooling temperature is in the range of 200 to 300° C. In another embodiment, To is such that the supercooling temperature is in the range of 225 to 275° C. In yet another embodiment, To is such that the supercooling temperature is in the range of 235 to 265° C. In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.25 to 0.5. In another embodiment, To is such that the normalized supercooling temperature is in the range of 0.3 to 0.4. In yet another embodiment, To is such that the normalized supercooling temperature is in the range of 0.325 to 0.375. 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 large ΔTx and a capability to be formed in bulk dimensions would be suitable for “thermoplastic” shaping of bulk articles. Discovering compositional regions where the alloy demonstrates a high glass forming ability is unpredictable. Discovering compositional regions where the metallic glass formed from an alloy demonstrates a large ΔTx is equally unpredictable. Discovering compositional regions where (1) the alloy demonstrates a high glass forming ability and (2) the metallic glass formed from the alloy demonstrates a large ΔTx is even more unpredictable than (1) and (2) independently. This is metallic glasses that are capable of being formed at bulk dimensions do not necessarily demonstrate a large ΔTx, and vice versa. In embodiments of the disclosure it is considered that a critical rod diameter of at least 3 mm for the disclosed alloys and a ΔTx of at least 45° C. for the metallic glasses formed from the disclosed alloys may be sufficient to enable “thermoplastic” shaping of bulk 3-dimensional articles. In other embodiments it is considered that a critical rod diameter of at least 3 mm for the disclosed alloys and a ΔTx of at least 50° C. for the metallic glasses formed from the disclosed alloys may be sufficient to enable “thermoplastic” shaping of bulk 3-dimensional articles. In yet other embodiments it is considered that a critical rod diameter of at least 5 mm for the disclosed alloys and a ΔTx of at least 50° C. for the metallic glasses formed from the disclosed alloys may be sufficient to enable “thermoplastic” shaping of bulk 3-dimensional articles.
In addition to glass-forming ability and thermal stability of the supercooled liquid, another important requirement for broad engineering applicability is the ability of the metallic glass to perform well under mechanical load. Good mechanical performance requires that the metallic glass has a relatively high fracture toughness. In the context of this disclosure, the mechanical performance of the metallic glass is characterized by a high fracture toughness and is quantified by the “critical bending diameter”. The critical bending diameter is defined as the maximum diameter in which a rod of the metallic glass, formed by water quenching a quartz capillary containing the molten alloy having a quartz wall thickness equal to about 10% of the rod diameter, can undergo macroscopic plastic bending without fracturing catastrophically.
Therefore, in some embodiments of the disclosure, the metallic glasses formed from the disclosed alloys demonstrate good mechanical performance in addition to exhibiting a large ΔTx and an ability to be formed in bulk dimensions. In the context of this disclosure it is considered that a critical bending diameter of at least 0.5 mm may be sufficient to ensure mechanical performance of the metallic glass.
In this disclosure, compositional regions in the Fe—Cr—Ni—Mo—P—C—B 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 rod diameter of at least 3 mm, while the metallic glasses formed from the alloys demonstrate a ΔTx of at least 45° C. In some embodiments, the critical rod diameter is at least 4 mm, in other embodiments 5 mm, in other embodiments 6 mm, while in other embodiments the critical rod diameter is at least 7 mm. In some embodiments, the thermal stability of the supercooled liquid is at least 47.5° C., in other embodiments at least 50° C., in other embodiments at least 52.5° C., while in other embodiments the thermal stability of the supercooled liquid is at least 55° C.
In some embodiments, the disclose Fe—Cr—Ni—Mo—P—C—B alloys demonstrate a large critical bending diameter, in addition to a high glass forming ability and a large ΔTx. In embodiments of the disclosure, the metallic glasses formed from the alloys demonstrate a critical bending diameter of at least 0.5 mm. In some embodiments, the critical bending diameter is at least 0.6 mm, in other embodiments at least 0.7 mm, while in other embodiments the critical bending diameter is at least 0.8 mm.
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 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 1200° C. In yet another embodiment, prior to quenching the molten alloy is heated to at least 1300° 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 inside a quartz crucible or a ceramic crucible. In other 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 alloy ingot is heated and melted under inert atmosphere. In one embodiment, 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 Fe—Cr—Ni—Mo—P—C—B alloys capable of forming metallic glasses. The alloys demonstrate a critical rod diameter of at least 3 mm, and the metallic glasses demonstrate a thermal stability of the supercooled liquid of at least 45° C.
Specifically, the disclosure provides Fe—Cr—Ni—Mo—P—C—B metallic glass-forming alloys and metallic glasses where the total metalloid concentration (i.e. the sum of P, C, and B concentrations) is confined over a narrow range, over which the alloys demonstrate a critical rod diameter of at least 3 mm, while the metallic glasses formed from the alloys demonstrate a thermal stability of the supercooled liquid of at least 45° C. In some embodiments, the metallic glasses formed from the alloys also demonstrate a critical bending diameter of at least 0.5 mm. In various embodiments of the disclosure, the concentration of metalloids ranges from 21.25 to 23.75 atomic percent. In other embodiments, the concentration of metalloids ranges from 21.5 to 23.5 atomic percent. In yet other embodiments, the concentration of metalloids ranges from 21.5 to 23 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):
Fe(100-a-b-c-d-e-f)CraNibMocPdCeBf EQ. (1)
In another embodiment of the metallic glass-forming alloy or metallic glass, a is up to 9, b ranges from 4 to 12, c ranges from 3 to 6.5, d+e+f ranges from 21.5 to 23.5, e ranges from 5.25 to 7.5, f ranges from 1.5 to 8.5, wherein the metallic glass-forming alloy has a critical rod diameter of at least 4 mm, and wherein the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 47.5° C.
In another embodiment of the metallic glass-forming alloy or metallic glass, a is up to 8, b ranges from 4.5 to 10, c ranges from 3.5 to 5.5, d+e+f ranges from 21.5 to 23, e ranges from 5.5 to 7, f ranges from 2 to 7.5, wherein the metallic glass-forming alloy has a critical rod diameter of at least 5 mm, and wherein the thermal stability of the supercooled liquid of the metallic glass against crystallization is at least 50° C.
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Fe67Ni7Mo4P19.5-xCxB2.5 are presented in Tables 1 and 2. In these alloys, P is substituted by C, where the atomic fraction of C varies from 4 to 8 percent, the atomic fraction of P varies from 11.5 to 15.5 percent, while the atomic fractions of Fe, Ni, Mo, and B are fixed at 67, 7, 4, and 2.5, respectively.
As shown in Table 1 and
The critical rod diameter of the example alloys according to the composition formula Fe67Ni7Mo4P19.5-xCxB2.5 is listed in Table 2 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula Fe67Ni7Mo4P19.5-xCxB2.5 is also listed in Table 2. As shown in Table 2, substituting P by C according to Fe67Ni7Mo4P19.5-xCxB2.5 results in increasing bending ductility. Specifically, the critical bending diameter increases from 0.7 mm for the metallic glasses containing 4-5 atomic percent C (Examples 1 and 2), to 0.8 mm for the metallic glasses containing 5.5-6.5 atomic percent C (Examples 3-5), to 0.9 mm for the metallic glasses containing 7-8 atomic percent C (Examples 6-8).
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Fe67Ni7Mo4P16-xC6Bx are presented in Tables 3 and 4. In these alloys, P is substituted by B, where the atomic fraction of B varies from 1 to 9 percent, the atomic fraction of P varies from 7 to 15 percent, while the atomic fractions of Fe, Ni, Mo, and C are fixed at 67, 7, 4, and 6, respectively.
As shown in Table 3 and
The critical rod diameter of the example alloys according to the composition formula Fe67Ni7Mo4P16-xC6Bx is listed in Table 4 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula Fe67Ni7Mo4P16-xC6Bx is also listed in Table 4. As shown in Table 4, substituting P by B according to Fe67Ni7Mo4P16-xC6Bx results in decreasing bending ductility. Specifically, the critical bending diameter decreases from 0.8 mm for the metallic glasses containing 1-2.5 atomic percent B (Examples 4 and 9-11), to 0.6 mm for the metallic glasses containing 3-4 atomic percent B (Examples 12-14), to 0.4 mm for the metallic glasses containing 5-7 atomic percent B (Examples 15-17), to 0.3 mm for the metallic glasses containing 8-9 atomic percent B (Examples 18 and 19).
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Fe71-xNi7MoxP13.5C6B2.5 are presented in Tables 5 and 6. In these alloys, Fe is substituted by Mo, where the atomic fraction of Mo varies from 2 to 7 percent, the atomic fraction of Fe varies from 64 to 69 percent, while the atomic fractions of Ni, P, C, and B are fixed at 7, 13.5, 6, and 2.5, respectively.
As shown in Table 5 and
The critical rod diameter of the example alloys according to the composition formula Fe71-xNi7MoxP13.5C6B2.5 is listed in Table 6 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula Fe71-xNi7MoxP13.5C6B2.5 is also listed in Table 6. As shown in Table 6, substituting Fe by Mo according to Fe71-xNi7MoxP13.5C6B2.5 results in decreasing bending ductility. Specifically, the critical bending diameter decreases from 1.0 mm for the metallic glass containing 2 atomic percent Mo (Example 20), to 0.9 mm for the metallic glass containing 3 atomic percent Mo (Example 21), to 0.8 mm for the metallic glass containing 4 atomic percent Mo (Example 4), to 0.7 mm for the metallic glasses containing 4.5-5 atomic percent Mo (Examples 22 and 23), to 0.6 mm for the metallic glass containing 6 atomic percent Mo (Example 24), to 0.5 mm for the metallic glass containing 7 atomic percent Mo (Example 25).
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Fe74-xNixMo4P13.5C6B2.5 are presented in Tables 5 and 6. In these alloys, Fe is substituted by Ni, where the atomic fraction of Ni varies from 3 to 13 percent, the atomic fraction of Fe varies from 61 to 71 percent, while the atomic fractions of Mo, P, C, and B are fixed at 4, 13.5, 6, and 2.5, respectively.
As shown in Table 7 and
The critical rod diameter of the example alloys according to the composition formula Fe74-xNixMo4P13.5C6B2.5 is listed in Table 8 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula Fe74-xNixMo4P13.5C6B2.5 is also listed in Table 8. As shown in Table 8, substituting Fe by Ni according to Fe74-xNixMo4P13.5C6B2.5 results in fairly constant bending ductility. Specifically, the critical bending diameter increases slightly from 0.8 mm for the metallic glasses containing 3-7 atomic percent Ni (Examples 26-28 and 4), to 0.9 mm for the metallic glasses containing 9-13 atomic percent Ni (Examples 29-31).
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula Fe65-xNi9CrxMo4P13.5C6B2.5 are presented in Tables 5 and 6. In these alloys, Cr is introduced at the expense of Fe, where the atomic fraction of Cr varies from 0 to 10 percent, the atomic fraction of Fe varies from 55 to 65 percent, while the atomic fractions of Ni, Mo, P, C, and B are fixed at 9, 4, 13.5, 6, and 2.5, respectively.
As shown in Table 9 and
The critical rod diameter of the example alloys according to the composition formula Fe65-xNi9CrxMo4P13.5C6B2.5 is listed in Table 10 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula Fe65-xNi9CrxMo4P13.5C6B2.5 is also listed in Table 10. As shown in Table 10, introducing Cr at the expense of Fe according to Fe65-xNi9CrxMo4P13.5C6B2.5 results in decreasing bending ductility. Specifically, the critical bending diameter decreases from 0.9 mm for the Cr-free metallic glass (Example 29), to 0.7 mm for the metallic glasses containing 1-1.5 atomic percent Cr (Examples 32 and 33), to 0.6 mm for the metallic glass containing 2 atomic percent Cr (Example 34)), to 0.5 mm for the metallic glass containing 3 atomic percent Cr (Example 35), to 0.4 mm for the metallic glass containing 4 atomic percent Cr (Example 36), to 0.3 mm for the metallic glasses containing 6-10 atomic percent Cr (Examples 37-40).
Specific embodiments of metallic glasses formed of metallic glass-forming alloys with compositions according to the formula [Fe0.814Ni0.116Cr0.019Mo0.051]100-x[P0.613C0.273B0.114]x are presented in Tables 11 and 12. In these alloys, metals are substituted by metalloids, where the atomic fraction of metalloids (combined fractions of P, C, and B), denoted by x, varies from 21 to 24 percent, while the atomic fraction of metals (combined atomic fractions Fe, Ni, Cr, Mo), (1−x), varies from 76 to 79 percent.
As shown in Table 11 and
The critical rod diameter of the example alloys according to the composition formula [Fe0.814Ni0.116Cr0.019Mo0.051]100-x[P0.613C0.273B0.114]x is listed in Table 12 and is plotted in
The critical bending diameter of the example metallic glasses according to the composition formula [Fe0.814Ni0.116Cr0.019Mo0.051]100-x[P0.613C0.273B0.114]x is also listed in Table 12. As shown in Table 12, substituting metals by metalloids according to [Fe0.814Ni0.116Cr0.019Mo0.051]100-x[P0.613C0.273B0.114]x results in decreasing bending ductility. Specifically, the critical bending diameter decreases from 0.8 mm for the metallic glasses containing 21-21.5 atomic percent metalloids x (Examples 41 and 42), to 0.7 mm for the metallic glasses containing 21.75-22.5 atomic percent metalloids x (Examples 33, 43 and 44), to 0.6 mm for the metallic glasses containing 23-23.5 atomic percent metalloids x (Examples 45 and 46), to 0.5 mm for the metallic glass containing 24 atomic percent metalloids x (Example 47).
Description of Methods of Processing the Example Alloys
The particular method for producing the alloy ingots involves inductive melting of the appropriate amounts of elemental constituents in a quartz tube under inert atmosphere. The purity levels of the constituent elements were as follows: Fe 99.95%, Cr 99.996% (crystalline), Ni 99.995%, Mo 99.95%, P 99.9999%, C 99.9995%, and B 99.5%. The melting crucible may alternatively be a ceramic such as alumina or zirconia, graphite, sintered crystalline silica, or a water-cooled hearth made of copper or silver.
The particular method for producing the rods of metallic glasses from the alloy ingots involves re-melting the alloy ingots in quartz tubes having 0.5 mm thick walls in a furnace at 1350° C. under high purity argon and rapidly quenching in a room-temperature water bath. Alternatively, the bath could be ice water or oil. Metallic glass articles could be alternatively formed by injecting or pouring the molten alloy into a metal mold. The mold could be made of copper, brass, or steel, among other materials.
In some embodiments, prior to producing a metallic glass article, the alloyed ingots could be fluxed with a reducing agent by re-melting the ingots in a quartz tube under inert atmosphere, bringing the alloy melt in contact with the molten reducing agent, and allowing the two melts to interact for about 1000 s at a temperature of about 1200° C. or higher, and subsequently water quenching. In one embodiment, the reducing agent is boron oxide.
Test Methodology for Assessing Glass-Forming Ability
The glass-forming ability of each alloy was assessed by determining the maximum rod diameter in which the amorphous phase of the alloy (i.e. the metallic glass phase) could be formed when processed by the methods described above. X-ray diffraction with Cu-Kα radiation was performed to verify the amorphous structure of the alloys.
Test Methodology for Assessing Bending Ductility
The bending ductility of each metallic glass was assessed by determining the maximum rod diameter in which the metallic glass subject to a bending load is capable of permanently (i.e. irreversibly, inelastically) bending without fracturing catastrophically.
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 and crystallization temperatures of sample metallic glasses formed from the glass-forming alloys, and also to determine the solidus and liquidus temperatures of the alloys.
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 disclosure. 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. Additionally, a number of well-known processes and elements have not been described in order to avoid unnecessarily obscuring the disclosure.
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.
The present application claims priority under 35 U.S.C. 119(e) to U.S. Provisional Application No. 62/805,845, entitled “Tough Iron-Based Glasses with High Glass Forming Ability and High Thermal Stability” to Na et al., filed Feb. 14, 2019, the disclosure of which is incorporated herein by reference in its entirety.
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| Number | Date | Country | |
|---|---|---|---|
| 20200263267 A1 | Aug 2020 | US |
| Number | Date | Country | |
|---|---|---|---|
| 62805845 | Feb 2019 | US |
