Patent Publication Number: US-2022212254-A1

Title: Hypoeutectic Amorphous Metal-Based Materials for Additive Manufacturing

Description:
CROSS-REFERENCE TO RELATED APPLICATIONS 
     The present application is a continuation of U.S. patent application Ser. No. 15/989,083, entitled “Hypoeutectic Amorphous Metal-Based Materials for Additive Manufacturing,” filed May 24, 2018, which claims priority to U.S. Provisional Application No. 62/510,618, entitled “Systems and Methods for Developing Tough Amorphous Metal-Based Materials for Additive Manufacturing”, filed May 24, 2017, the disclosures of which are incorporated herein by reference in their entireties. 
    
    
     STATEMENT OF FEDERAL FUNDING 
     The invention described herein was made in the performance of work under a NASA contract NNN12AA01C, and is subject to the provisions of Public Law 96-517 (35 USC 202) in which the Contractor has elected to retain title. 
     FIELD OF THE INVENTION 
     The present invention generally relates to bulk amorphous metal materials and parts with improved toughness and methods of manufacture thereof from hypoeutectic bulk amorphous metal materials. 
     BACKGROUND OF THE INVENTION 
     Amorphous metals, also known as metallic glasses or glassy metals, are solid, metal-based alloy materials with a disordered and, therefore, glass-like atomic-scale structure, in contrast to the highly ordered atomic structure of conventional crystalline metal materials. Amorphous metal alloy formulations are typically very complex and precisely composed of one main (predominant in the amount) metal (M) and one or more other metal or non-metal elements to allow for the melts of these materials to be quenched into a vitreous state and avoid crystallization upon cooling. The metallic glass alloys that can be cast (with reasonable cooling rates) into a relatively large thickness (generally over 1 mm) without pronounced crystallization are called bulk metallic glasses (BMGs). On the other hand, an in-situ composite or bulk metallic glass matrix composite (BMGMC) is defined as an alloy which, upon rapid cooling (1-1000 K/s), chemically partitions into two or more phases, one being an amorphous matrix and the other(s) being crystalline inclusions. 
     In principle, metallic glasses possess a number of useful material properties that can allow them to be implemented as highly effective engineering materials. For example, metallic glasses are generally much harder than conventional metals, and are generally tougher than ceramic materials. BMGs are also relatively corrosion resistant, and, unlike conventional silicate glass, they can have good electrical conductivity. Importantly, the manufacture of metallic glass materials lends itself to relatively easy processing and, in particular, the manufacture of a metallic glass can be compatible with an injection molding process or any similar casting process. Other metallic glass manufacturing processes include physical vapor deposition, solid-state reactions, ion irradiation, and mechanical alloying. 
     Metal additive manufacturing, also commonly known as metal 3D printing, is an emerging manufacturing technology, which is being rapidly integrated into commercial applications, such as fabrication of nozzles in aircraft and rocket engines. Typically, a 3D printing process comprises sequential deposition of a multitude of thin layers of a material to assemble a desired bulk part or structure. The most common forms of metal additive manufacturing are powder bed fusion and directed energy deposition. Other emerging techniques include thermal spray additive manufacturing, laser foil welding, fused filament fabrication, binder jetting, direct metal jetting, and ultrasonic additive manufacturing. Recently, it has been shown that bulk metallic glass parts can also be fabricated by additive manufacturing using a variety of methods. 
     SUMMARY OF THE INVENTION 
     Embodiments of the invention are directed to bulk amorphous metal materials and parts with improved toughness and methods of manufacture thereof from hypoeutectic bulk amorphous metal materials. 
     Many embodiments are directed to methods of additive manufacturing a bulk amorphous metal part including:
         providing a metallic glass forming alloy based on a metallic glass-forming alloy system with two or more components where a eutectic exists between two of the components that results in a eutectic metallic glass forming alloy having a critical casting thickness, and wherein the amount of at least the most abundant component of the metallic glass-alloy system is increased at the expense of the sum of the other components such that the metallic glass forming alloy is hypoeutectic and has a critical casting thickness less than the eutectic metallic glass forming alloy;   disposing molten layers of the hypoeutectic metallic glass forming alloy atop one another additively, and allowing said layers to cool to a bulk amorphous metal part having an amorphous fraction of at least 10% by volume, having an overall thickness of at least 1 mm; and   wherein the most abundant component of the metallic glass forming alloy comprises at least 70% atomic the metallic glass forming alloy.       

     In other embodiments, the metallic glass forming alloy is heated to above its melting temperature and then cooled at an initial cooling rate faster than 1,000 K/s such that each layer being disposed cools sufficiently rapidly so as to form at least a partially amorphous metal layer. 
     In still other embodiments, the additive manufacturing process is selected from the group of powder bed fusion, directed energy deposition, electron beam melting, wire-fed melting, fused deposition modeling, thermal spray additive manufacturing, laser foil printing, molten metal printing, ultrasonic additive manufacturing, and drop on demand printing. 
     In yet other embodiments, the metallic glass forming alloy of the bulk amorphous metal part has a fragility at least 5% higher as measured through differential scanning calorimetry than that of the eutectic metallic glass forming alloy using the same primary two components. 
     In still yet other embodiments, the eutectic metallic glass forming alloy has a critical casting thickness of greater than 1 mm, and the metallic glass forming alloy has a glass forming ability less than approximately 1 mm. 
     In still yet other embodiments, the metallic glass forming alloy of the bulk amorphous metal part has a shear modulus at least 5% lower than that of the eutectic metallic glass forming alloy. 
     In still yet other embodiments, the metallic glass forming alloy has a composition that is at least 5% different in the amount of the primary component from the eutectic metallic glass forming alloy. 
     In still yet other embodiments, the disposition is conducted under an inert gas. 
     In still yet other embodiments, the metallic glass forming alloy is combined with a crystalline phase to form a composite which when deposited alters the fracture toughness of the bulk amorphous metal part as compared to a bulk amorphous metal part formed using a fully amorphous metallic glass forming alloy. 
     In still yet other embodiments, the metallic glass forming alloy and the crystalline phase are in the form of powders with a size distribution within 10% of each other. 
     In still yet other embodiments, the metallic glass forming alloy and the crystalline phase have different melting temperatures such that during disposition of the metallic glass forming alloy melts and the crystalline phase at most partially melts. 
     In still yet other embodiments, the bulk amorphous metal part the metallic glass forming alloy and crystalline phase have at least 5% ductility in a tension test. 
     In still yet other embodiments, the notch toughness of the bulk amorphous metal part is at least 60 MPa m 1/2  as measured on a notched 3 mm thick sample using standard three-point-bending toughness measurements with a 100 micrometer root radius notch. 
     In still yet other embodiments, Zr is the most abundant component of the metallic glass forming alloy. 
     In still yet other embodiments, the metallic glass forming alloy contains Zr—Cu—Ni—Al and has a concentration of zirconium 70-85%, nickel 5-15%, copper 1-5% and Al 2-7% in atomic percentages. 
     In still yet other embodiments, the metallic glass forming alloy is a metallic glass-forming alloy system selected from the group of Zr—Cu—Al—X, Zr—Al—X, Pt—Cu—P—X, Pt—P—X, Pt—Si—B—X, Pd—P—X, Ni—Ti—Zr—X, Fe—P—X, Fe—B—X, Ti—Zr—X, Ti—Cu—X, where X is one or more optional additional component elements. 
     In still yet other embodiments, the metallic glass forming alloy is selected from one of the following: has at least 77% atomic of platinum, has at least 80% atomic of palladium, has at least 60 atomic % of copper, has at least 75% atomic of nickel, has at least 80% atomic of iron, has at least 50% atomic of titanium, has at least 80% atomic of gold, has at least 88% atomic of aluminum, has at least 62% atomic of hafnium, or has at least 50% atomic of tantalum. 
     In still yet other embodiments, the amount of the most abundant metal in the metallic glass forming alloy is at least 5% atomic more than the amount in a metallic glass forming alloy made from the same constituents but with the highest possible glass forming ability. 
     In still yet other embodiments, the bulk amorphous metal part has a relative density compared to the solid of at least 99.5%. 
     In still yet other embodiments, the fragility of the metallic glass forming alloy selected for disposition is at least 50. 
     In still yet other embodiments, the thickness of each disposed layer is between 1-250 micrometers. 
     In still yet other embodiments, the metallic glass forming alloy is consolidated during disposition as an amorphous feedstock material that is amorphous and retains the amorphous character and high toughness after disposition. 
     In still yet other embodiments, the additive disposition process is selected from the group consisting of cold spraying, ultrasonic additive manufacturing, binder jetting, sintering, metal injection molding, and powder consolidation. 
     In still yet other embodiments, the amorphous feedstock material is in a form selected from the group consisting of wire, sheet and ribbon. 
     In still yet other embodiments, the method further includes allowing each disposed layer to cool prior to disposition of a further layer thereon. 
     In still yet other embodiments, each disposed layer is allowed to cool sufficiently to prevent annealing of said disposed layer during disposition of a layer thereon. 
     In still yet other embodiments, the disposing includes one of either extending the time between the disposition of each layer, or increasing the rate of heating of each layer. 
     In still yet other embodiments, the most abundant metal of the metallic glass-forming alloy comprises up to the three most abundant metals of the metallic glass-forming alloys. 
     In still yet other embodiments, the amount of the most abundant metal is increased at the expense of metals of the metallic glass forming alloy to the right of the most abundant metal on the periodic table. 
     In still yet other embodiments, the bulk metallic part is selected from the group of gears, strain wave gears, knives, cutting tools, bearings, inserts, fasteners, mechanisms, golf clubs, electronic casings, watches, structural coatings, springs, brackets, spacecraft components, and jewelry. 
     Many other embodiments are directed to methods of additive manufacturing a bulk amorphous metal part including:
         providing a metallic glass forming alloy based on a metallic glass-forming alloy system with two or more components where a eutectic exists between two of the components that results in a eutectic metallic glass forming alloy having a critical casting thickness, and wherein the amount of at least the most abundant component of the metallic glass-alloy system is increased at the expense of the sum of the other components such that the metallic glass forming alloy is hypoeutectic and has a critical casting thickness less than the eutectic metallic glass forming alloy;   disposing molten layers of the hypoeutectic metallic glass forming alloy atop one another additively, and allowing said layers to cool to a bulk amorphous metal part having an amorphous fraction of at least 10% by volume, having an overall thickness of at least 1 mm; and   wherein the most abundant component of the metallic glass forming alloy comprises at least 70% atomic the metallic glass forming alloy.       

     Still many other embodiments are directed to methods of additive manufacturing a bulk amorphous metal part including:
         providing a metallic glass forming alloy based on a metallic glass-forming alloy system with at least one component from the early transition metals and at least one other component from the non-early transition metals where a eutectic exists between the at least two components that results in a eutectic metallic glass forming alloy having a critical casting thickness, and wherein the amount of at least the components from the early transition metals of the metallic glass-alloy system are increased at the expense of the sum of the other components such that the metallic glass forming alloy is hypoeutectic and has a critical casting thickness less than the eutectic metallic glass forming alloy;   disposing molten layers of the hypoeutectic metallic glass forming alloy onto a build plate atop one another additively, and allowing said layers to cool to a bulk amorphous metal part having an amorphous fraction of at least 10% by volume, having an overall thickness of at least 1 mm, and having a density of at least 99.8%;   wherein the disposition occurs at a rate to prevent annealing of each disposed layer by the disposition of an overlaid layer; and   wherein the early transition metal components of the metallic glass forming alloy comprise at least 70% atomic the metallic glass forming alloy.       

     In other embodiments, the disposing includes one of either extending the time between the disposition of each layer, or increasing the rate of heating of each layer to prevent annealing of each disposed layer during disposition of the overlaid layer. 
     In still other embodiments, the method includes heating the build plate to within 10% of the glass transition temperature of the metallic glass-forming alloy. 
     Additional embodiments and features are set forth in part in the description that follows, and in part will become apparent to those skilled in the art upon examination of the specification or may be learned by the practice of the disclosed subject matter. A further understanding of the nature and advantages of the present disclosure may be realized by reference to the remaining portions of the specification and the drawings, which forms a part of this disclosure. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
       These and other features and advantages of the present invention will be better understood by reference to the following detailed description when considered in conjunction with the accompanying data and figures, wherein: 
         FIG. 1A  provides plots of notch toughness vs. critical rod diameter for exemplary alloys according to the prior art. 
         FIG. 1B  provides plots of notch toughness and critical rod diameter vs. shear modulus for exemplary amendment according to the prior art. 
         FIGS. 2A and 2B  provide schematics of a process for additive manufacturing of amorphous based metal materials in accordance with embodiments of the invention. 
         FIG. 3A  provides schematic plots of notch toughness to critical casting thickness in accordance with embodiments of the invention. 
         FIG. 3B  provides a table of physical properties for exemplary alloys in accordance with embodiments of the invention. 
         FIG. 4  provides a schematic of properties for metallic glasses for use in accordance with embodiments of the invention. 
         FIGS. 5A to 5C  provide schematic plots of ( 5 A) fragility, ( 5 B) shear modulus and ( 5 C) glass forming ability for compositions for use in accordance with embodiments of the invention. 
         FIGS. 6A and 6B  provide tables providing properties of exemplary alloys in accordance with embodiments of the invention. 
         FIGS. 6C to 6E  provide plots showing the correlation between fragility and glass forming ability of exemplary metallic glass alloys in accordance with embodiments of the invention. 
         FIGS. 7A and 7B  provide plots showing how fragility can be used to predict glass forming ability for exemplary alloys in accordance with embodiments of the invention. 
         FIG. 8  provides a flow chart of a process for selecting and additively manufacturing metallic glass alloys in accordance with embodiments of the invention. 
         FIG. 9  provides a schematic of a temperature time diagram of the critical cooling rate for forming a metallic glass in accordance with embodiments of the invention. 
         FIGS. 10A and 10B  provide schematics of a method for 3D printing metallic glasses ( 10 A), and a diagram showing the relation of the embrittlement of such materials ( 10 B), in accordance with embodiments of the invention. 
         FIG. 11  provides a plot showing the fragility of metallic glasses vs annealing sensitivity in accordance with embodiments of the invention. 
         FIG. 12  provides a schematic diagram of the relationship of the notch toughness of metallic glass materials for different forming methods in accordance with embodiments of the invention. 
         FIG. 13  provides a flow chart of a method for printing a metallic glass material in accordance with embodiments of the invention. 
         FIGS. 14A to 14 -H provide tables of properties for hypoeutectic metallic glass materials in accordance with embodiments of the invention. 
         FIGS. 14I-1 and 14I-2  provide tables of properties for hypoeutectic metallic glass materials in accordance with embodiments of the invention. 
         FIG. 15  provides a plot showing the result of printing a metallic glass part according to the prior art. 
     
    
    
     DETAILED DISCLOSURE 
     Turning to the drawings and data, systems and methods for developing tough hypoeutectic amorphous metal-based materials for additive manufacturing, and methods of additive manufacturing using such materials are provided. It will be understood that the embodiments of the invention described herein are not intended to be exhaustive or to limit the invention to precise forms disclosed. Rather, the embodiments selected for description have been chosen to enable one skilled in the art to practice the invention. 
     Amorphous metals, also known as metallic glasses, are relatively new materials possessing a unique combination of advantageous properties that makes them attractive candidates for a wide variety of applications, including gears, strain wave gears, and other useful parts and mechanisms. (See, e.g., U.S. patent application Ser. Nos. 13/928,109; 14/177,608; 14/259,608; 14/491,618; 15/062,989; and Ser. No. 15/918,831, the disclosures of which are incorporated herein by reference.) For example, these materials typically exhibit excellent corrosion and wear resistance, high strength and high hardness, yet, simultaneously, substantial elasticity. Moreover, manufacturing of parts from metallic glass alloys is, in principle, compatible with such straightforward processes as injection molding or similar casting processes. However, forming of amorphous metals into useful parts remains challenging, especially in the production of parts with dimensions exceeding 1 mm, due to the limitations associated with the need for extremely high cooling rates necessary for quenching of the metallic glass melts into vitreous state, wherein the glassy melt must be solidified faster than competing crystallization can occur. Therefore, bulkier (thicker) parts, which require longer time to fully cool and solidify, are more difficult to manufacture without loss of advantageous properties afforded by the glassy phase. 
     One parameter used to characterize the glass forming ability (GFA) of an alloy is the “critical rod dimeter” (d c ), wherein the better glass formers are able to yield thicker (i.e. having larger critical rod diameters), fully amorphous parts at a given cooling rates. Another way of framing the glass forming ability of an amorphous metal is by the minimum cooling rate required for material to form an amorphous phase, this “critical cooling rate” determines the types of manufacturing processes available. For example, very poor glass forming materials can have critical cooling rates as high as 10 6 ° C./s. Another parameter that relates to the glass forming of a material is fragility. Fragility characterizes how rapidly the dynamics of a material slow down as it is cooled toward the glass transition: materials with a higher fragility have a relatively narrow glass transition temperature range, while those with low fragility have a relatively broad glass transition temperature range. The most common definition of fragility is the “kinetic fragility index” m, which characterizes the slope of the viscosity (or relaxation time) of a material with temperature as it approaches the glass transition temperature from above. Physically, fragility may be related to the presence of dynamical heterogeneity in glasses, as well as to the breakdown of the usual Stokes-Einstein relationship between viscosity and diffusion. 
     When a material is placed under stress and has reached the limit of its strength, it usually has the option of either deformation or fracture. A number of parameters may be used to describe the strength of a metallic glass when placed under stress, including: toughness, brittleness, fragility, etc. Toughness is the ability of a material to absorb energy and plastically deform without fracturing. One definition of material toughness is the amount of energy per unit volume that a material can absorb before rupturing. It is also defined as a material&#39;s resistance to fracture when stressed. Toughness generally requires a balance of strength and ductility. In general terms, a material is considered brittle if, when subjected to stress, it breaks without significant plastic deformation. Brittle materials absorb relatively little energy prior to fracture, even those of high strength. 
     One approach to improving glass forming ability and increasing critical rod diameter of metallic glass alloys is to dilute the alloy&#39;s predominant/base metal (M) with other metal or non-metal elements, thus, decreasing the alloy&#39;s overall propensity for metallic crystallization. The basic strategy is to move the composition closer to a eutectic point, where a deep melting temperature allows for more rapid cooling to form a glass. However, the better glass formers (with thicker critical rod diameters at the expense of lower main metal content) resulting from this approach typically make less tough materials. For example,  FIG. 1A  demonstrates that, for a given chemical family of alloys, the material toughness declines roughly linearly with the increase in critical rod diameter (i.e. glass forming ability). Furthermore,  FIG. 1B  demonstrates that the shear modulus (G, which is the deformation of a solid when it experiences a force parallel to one of its surfaces while its opposite face experiences an opposing force) and the barrier to shear flow (W), which are the intrinsic parameters that govern the toughness of metallic glasses, wherein W is proportional to G, are also dependent on the alloy&#39;s glass forming ability/critical rod diameter. 
     Alternatively, in instances when the toughness of the material cannot be compromised, the manufacturing of metallic glass parts must rely solely on fast cooling processes, such as, for example, one of: die casting, injection molding, melt spinning, thermal spraying, atomization, suction casting, arc melting, and induction melting. Recently, additive manufacturing processes (known as 3D printing) have also been utilized to form bulk amorphous metals parts. For example, 3D printing processes such as powder bed fusion, thermal spray additive manufacturing, laser foil welding, direct metal laser sintering, directed energy deposition, fused filament fabrication, liquid jetting, and ultrasonic additive manufacturing have all been used to manufacture bulk metallic glass parts. Notably, in the manufacturing of parts from metallic glass alloys, most additive manufacturing techniques offer significant advantages over casting methods, because the overall part is formed from a plurality of discrete layers, wherein each layer can potentially have a thickness (as low as 250 microns or less) that is less than the critical rod diameter of a given metallic glass alloy. Coincidently, printing thinner layers enables much faster per-layer cooling rates. Specifically, in most standard 3D printing processes, a layer can be cooled at a rate as fast as between 1,000 to 100,000 K/s, which is fast enough to print a fully amorphous metallic glass layer even from a metallic glass alloy with a critical rod dimeter of less than 1 mm. Accordingly, it has been shown that 3D printing techniques allow for manufacturing of fully amorphous metallic glass parts in overall thicknesses that might exceed the glass forming ability of a given alloy (and, therefore, cannot be achieved by casting methods), without any compromise to the physical and mechanical properties of the alloys, including toughness. 
     Nevertheless, in general and regardless of the manufacturing method, the toughness of metallic glass alloys parts is typically inferior to that of many other high performance conventional metallic alloys that can also be used in 3D printing, such as, for example, aluminum, titanium, steel, Inconel, nickel, or even certain metal matrix composites. Specifically, BMGs are notoriously brittle in tension tests and have moderate to low resistance to fracturing in bending. Therefore, it is highly desirable to develop amorphous metal alloys that are both amenable to 3D printing and have a well-balanced combination of physical and mechanical properties, including both high strength and at least moderate toughness as measured through notch toughness measurements or bending tests. More specifically, it is desirable to develop a metallic glass alloys with a notch toughness of at least 60 MPa m 1/2  or above, which would be a sufficient toughness for a BMG part to be useable in structural applications without being too brittle. Specifically, the toughness of at least 60 MPa m 1/2  or greater is large enough to ensure that the part is sufficiently ductile in bending to be useful in a wide assortment of components. In other words, a four point bending tests of a BMG produced according to the disclosed method would exhibit plasticity in bending prior to failure. For example, a bulk amorphous metal part with a toughness greater than 60 MPa m 1/2  can be bent permanently in a rod of up to 4 mm in diameter as measured using a standard three-point-bending toughness measurements with a 100 micrometer root radius notch. 
     However, although cast BMG parts have been shown to have notch toughness above the 60 MPa m 1/2 , no additively manufactured BMG part has featured toughness that is above this threshold. Accordingly, although it has been shown that additive manufacturing techniques, wherein a part is constructed from a multitude of thin, rapidly coolable layers, can be used with alloys that are poor glass formers to ultimately produce a fully amorphous bulk part with a thickness larger than one that could be cast from the same alloy, these prior attempts have always focused on achieving larger part thicknesses without loss of the amorphous phase (i.e. on preserving properties afforded by the amorphous phase) and never on improving any particular physical property of the alloy. For example, it has been shown that 3D printing can be used to make amorphous parts from inexpensive Fe-based alloys that cannot be cast to the same thickness. As such, 3D printed BMG parts reported to date typically have roughly the same physical properties as equivalent cast BMG parts (assuming the alloy can be cast at all), including inferior toughness. The prior art has demonstrated that metallic glass alloys that are already known from casting or coating have been successfully printed but no attempts to customize the alloy composition specifically for improving the properties of the printed parts has been demonstrated. The current disclosure is the first to suggest that the properties of printed BMGs can be improved by modifying well-known alloys specifically for printing. The prior art has focused on simply printing alloys that are known from previous work in casting, which has resulted in properties that are far from what can be optimally achieved with the alloy design strategy disclosed here. 
     Embodiments of Hypoeutectic Amorphous Metal-Forming Alloys 
     The current application is directed to embodiments of methods and systems of amorphous metal-forming alloys for fabrication of bulk amorphous metal parts via additive manufacturing with enhanced material properties (e.g., toughness) by modifying alloys away from well-known eutectic compositions with good glass formation and into hypoeutectic regions with lower glass forming ability but higher toughness. In many embodiments, the methods may take advantage of very fast rates of cooling afforded by the 3D printing of discrete thin layers during the assembly of bulk parts from metallic glass alloys with compositions selected to improve toughness at the expense of glass forming ability ( FIGS. 2A and 2B ) while maintain at least a partial amorphous character of the alloy (e.g., an amorphous fraction of at least 10% by volume for a part having an overall thickness of 1 mm). For example, in many embodiments, the cooling rate of a single 3D printed layer (which may be, for example, 250 microns or less) is at least 1,000 K/s or faster ( FIG. 2A ). 
     In many embodiments, the metallic glass alloy used in manufacturing of a bulk part is selected to have minimal glass forming ability for the per layer cooling rate afforded by the manufacturing process ( FIG. 2A ). In many embodiments, the metallic glass alloys used in embodiments are specially composed for high toughness. In many such embodiments, the alloy is a hypoeutectic metallic glass alloy and comprises higher main metal content than the corresponding eutectic composition. In many such embodiments, the hypoeutectic is formed by increasing the amount of at least the most abundant component of the metallic glass-alloy system at the expense of the sum of the other components. In various such embodiments the composition is at least 5% different in the amount of the primary component from the eutectic metallic glass forming alloy. 
     Furthermore, in many embodiments, bulk amorphous metal glass parts are 3D printed from hypoeutectic alloys with inferior glass forming ability as compared to an alloy with the same elements but nearer to the eutectic composition, such that the resulting parts possess higher toughness than the nearest analog parts cast from the alloys with acceptable glass forming ability. In many such embodiments the notch toughness of parts additively manufactured from metallic glass materials according to the methods of the application is at least 60 MPa m 1/2  ( FIG. 2B ) as measured on a notched 3 mm thick sample using a standard three-point-bending toughness measurements with a 100 micrometer root radius notch. In many such embodiments, the glass forming ability of an alloy is sacrificed (in order to improve its toughness) by increasing the content of the main metal or the main two to three metals in the alloy&#39;s composition. In many embodiments, such composition adjustments dramatically increase both the fragility and toughness of a given alloy, along with decreasing its glass forming ability down to below the thickness where it can be directly cast into bulk parts. Therefore, in many embodiments, additive manufacturing is, in turn, used to compensate for the poor glass forming ability of such tough hypoeutectic alloys by printing very thin (thinner than the critical rod diameter) discrete layers amenable to very fast cooling and further assembly into bulk fully amorphous parts. Consequently, in many embodiments, the weak glass forming but extremely tough hypoeutectic metallic glass alloys formulated according to the methods of the application are used in appropriate combination with additive manufacturing techniques to fabricate bulk amorphous metal parts that have toughness greater than any equivalent or nearest equivalent cast parts made from the same constituent materials. In many embodiments, the methods of the application are globally applicable across all bulk glass forming alloy families, because the physics of fragility and off eutectic glass formation are universal. 
     Embodiments of Methods for Selecting Amorphous Metal Alloy Compositions 
     Many embodiments comprise an alloy based on a metallic glass forming alloy system with at least one component from the early transition metals and at least one other component from the non-early transition metals, where a eutectic exists between the at least two components that results in a eutectic metallic glass forming alloy having a critical casting thickness. The toughness of metallic glass alloys selected for the additive manufacturing of tough parts is enhanced according to embodiments by increasing the content of the main metal (i.e., the metal with the highest concentration), or the main two to three metals (i.e., the metals with the highest few concentrations), within the alloys&#39; compositions at the expense of the other, glass formation enhancing, elements to form a hypoeutectic alloy material. Typically, this would entail decreasing the amount of the late transition metal or the metalloids in the alloy composition in favor of the early transition metal atoms. However, it could also entail decreasing the amount of non-metallic elements in favor of the metallic ones, as in the case of increasing the compositional content of Au, Pd, Pt, Ag at the cost of P, B, Si, C, Be, for example. It could also entail increasing the amount of elements such as Zr, Ti, Hf, Nb, V, Ta at the cost of Cu, Ni, Al, Be, B, P, Si, C, etc. 
     In general, as is known in the art and illustrated by  FIG. 3A , increasing the main metal (M) content (A, B, C) at the expense of other alloy components (X, Y, Z) typically decreases the alloys&#39; glass forming ability (GFA) and increases its fragility and, therefore, increases its toughness. This can also be thought of differently as shifting the composition away from the lowest melting point, or eutectic composition, of the alloy towards a higher melting temperature, more metal-rich region. Here, it should be noted that, since it is difficult to obtain cast samples for alloys with critical rod diameter of less than 1-2 mm (such as the alloys of this application), the toughness of bulk parts made from such alloys is very difficult or even impossible to measure directly using standard mechanical tests. However, multiple indirect studies indicate that the trend, wherein the alloy&#39;s toughness increases with decreasing critical rod diameter within a single alloy compositional family, continues past the critical rod diameter values that allow casting of bulk parts for mechanical measurements. In addition to mechanical properties, such as toughness, physical properties of the glass, such as fragility, also increase with decreasing critical rod diameter in a single family. 
     As a specific example, the table in  FIG. 3B  illustrates the dependence of GFA/critical rod diameter on the concentration of M for an alloy system of Zr—Cu—Al—Ni alloys (M=Zr).  FIG. 3B  shows that the GFA quickly diminishes (from d c  of over 10 mm to −5 mm) as Zr content is increased (from 53-57 atomic percent to 70 atomic percent). Furthermore, it is expected that in any alloy family the alloy with the highest M content (Zr 70 ) will have the highest toughness, as demonstrated in the series presented in  FIG. 3B . Accordingly, in various embodiments the alloys are selected from the group of alloy families Zr—Cu—Al—X, Zr—Al—X, Pt—Cu—P—X, Pt—P—X, Pt—Si—B—X, Pd—P—X, Ni—Ti—Zr—X, Fe—P—X, Fe—B—X, Ti—Zr—X, Ti—Cu—X, where X is one or more optional additional elements. In other such embodiments Zr is the most abundant component of the metallic glass forming alloy. In other embodiments the metallic glass forming alloy contains Zr—Cu—Ni—Al. In some such embodiments the alloy has a concentration of zirconium 70-85%, nickel 5-15%, copper 1-5% and Al 2-7% in atomic percentages. In various other embodiments the metallic glass forming alloy is selected from one of the following: has at least 77% atomic of platinum, has at least 80% atomic of palladium, has at least 60 atomic % of copper, has at least 75% atomic of nickel, has at least 80% atomic of iron, has at least 50% atomic of titanium, has at least 80% atomic of gold, has at least 88% atomic of aluminum, has at least 62% atomic of hafnium, or has at least 50% atomic of tantalum. In some such embodiments the amount of the most abundant metal in the metallic glass forming alloy is at least 5% atomic more than the amount in a metallic glass forming alloy made from the same constituents but with the highest possible glass forming ability. 
     In short, alloy selection for 3D printing of tough bulk amorphous parts according to the embodiments and methods of the application are contrary to convention. To this end,  FIG. 4  illustrates a phase diagram for a hypothetical metallic glass alloy composition comprised of 2 elements—metal A and another (metal, non-metal, or metalloid) element B in accordance with embodiments. As shown in  FIG. 4 , the eutectic point is the metallic glass alloy composition at which, upon cooling, the material directly transitions from the liquid to the amorphous phase, completely avoiding crystallization. Therefore, alloys with eutectic or near eutectic compositions are the best glass formers (i.e., are the least sensitive to cooling rates). As such, moving away from a eutectic composition must be compensated with an increase in the cooling rate, so as to avoid crystallization of upon cooling. In addition to having the best glass forming abilities, the alloys with compositions near the eutectic point also have lower fragility, and are subsequently more brittle. Moving to the opposite side of the phase diagram to the hypereutectic compositions further decreases the fragility and leads to the most brittle glasses. In conventional teachings, metallic glass materials are selected to be as close to the eutectic as possible to maximize the glass forming properties, while still being tougher than the hypereutectic compositions. Accordingly, in many embodiments, the alloys of the instant applications have a hypoeutectic composition (i.e. a composition that is richer in the main metal than the corresponding eutectic composition), and are, thus, poorer glass formers (with critical rod diameter of equal to or less than 1 mm), requiring higher cooling rates to achieve fully amorphous state. In many such embodiments the hypoeutectic alloy has a composition that is at least 5% different in the amount of the primary component from the eutectic metallic glass forming alloy. 
     Furthermore, the hypoeutectic alloys of the instant application demonstrate higher fragility and toughness (when produced in bulk through additive manufacturing), as compared to their eutectic counterparts, produced through the same technique. This difference in properties can be expressed and quantified through a number of different physical parameters of the alloys and parts formed from such alloys. For example, in many embodiments the metallic glass forming alloy of the bulk amorphous metal part has a fragility at least 5% higher, as measured through differential scanning calorimetry, than that of the eutectic metallic glass forming alloy using the same primary two components. In some embodiments, the fragility of the metallic glass forming alloy selected for disposition is at least 50. In other embodiments, the metallic glass forming alloy of the bulk amorphous metal part has a shear modulus at least 5% lower than that of the eutectic metallic glass forming alloy. In other such embodiments the bulk amorphous metal part the metallic glass forming alloy and crystalline phase have at least 5% ductility in a tension test. In other embodiments, the notch toughness of the bulk amorphous metal part is at least 60 MPa m 1/2  as measured on a notched 3 mm thick sample using standard three-point-bending toughness measurements with a 100 micrometer root radius notch. 
       FIGS. 5A through 5C  further illustrate the properties expected for the hypoeutectic metallic glass alloys of this application. Specifically, as compared to the corresponding eutectic compositions or even hypereutectic (i.e. containing less of main metal) compositions, alloys of the instant application are expected to have the highest fragility ( FIG. 5A ), lowest shear modulus G ( FIG. 5B ), and correspondingly, the highest toughness ( FIG. 5B ). As a trade-off, the alloys of the application are expected to have a very low glass forming ability, with critical rod diameter of approximately 1 mm or less, which, of course, makes them unacceptable candidates for most forming methods, including casting and molding. For example, in many embodiments where the eutectic metallic glass forming alloy has a critical casting thickness of greater than 1 mm, the metallic glass forming alloy would have a glass forming ability less than approximately 1 mm. However, in many embodiments, the low GFA of the hypoeutectic alloys of the application is compensated by the fast cooling rates afforded by the additive manufacturing techniques employed in the manufacturing of bulk parts according to the methods of the application. Notably, as illustrated by  FIGS. 3B, 4 and 5C —going hypereutectic in an alloy composition (i.e. reducing the amount of main metal as compared to the eutectic composition) also reduces the GFA; however, only hypoeutectic alloys are expected to have improved toughness. 
     It should also be apparent that the designation of 1 mm for the glass forming ability of the hypoeutectic alloy is not critical but rather represents a minimum glass forming ability of the selected additive manufacturing technique. For example, the cooling rate for a specific metal additive manufacturing technique may vary such that the composition of the hypoeutectic BMG may have to be adjusted to better glass formers so as to achieve a glass during printing. Prior art has previously demonstrated that BMGs with glass forming ability of less than 1 mm could successfully be printed fully amorphous using powder bed fusion, laser foil printing, and thermal spray additive manufacturing. The glass forming ability, however, is highly correlated with the oxygen content of the metal powder. For example, a hypoeutectic BMG with a high percentage of oxygen may not have sufficient glass forming ability to be printed amorphous and thus the composition may have to be slightly compensated back towards the direction of the eutectic to achieve a glass during printing. 
     Importantly, in many embodiments, the fragility property may be used to predict the expected GFA and toughness of the hypoeutectic alloys of the instant application and aid in their selection. This criterion, which may be measured or estimate by standard means, is important for the methods of the instant application since the alloys best suited for the methods must have very low GFA, making it hard (if not impossible) to cast them into bulk parts for the applicable measurements.  FIGS. 6A through 6E  provide tables and plots that demonstrate the relationship between the BMG fragility, GFA, and toughness, and clearly demonstrate that the GFA and toughness of a glass forming alloy can be predicted from fragility or certain fragility dependent parameter measurements. More specifically, these figures demonstrate that the higher fragility in a given alloy family is indicative of lower glass forming ability and tougher bulk parts. More specifically, W. L. Johnson et. al. have conclusively shown with the data plots reproduced in  FIGS. 7A and 7B , that fragility and reduced glass transition temperature (Trg), the ratio between the liquidus temperature, and the glass transition temperature can be used to accurately calculate the GFA of alloys that cannot be cast into bulk samples due to poor GFA. (See W. L. Johnson et. al., Nature Communications, 7, Article number: 10313 (2016), the disclosures of which are incorporated herein by reference.)) 
     Accordingly, in many embodiments, the selection process of amorphous metal alloy compositions for additive manufacturing of bulk amorphous parts with superior toughness comprises following the sequence tabulated in  FIG. 8 . In many embodiments, first, an amorphous metal composition with a critical rod diameter of at least 1 mm and poor to moderate bulk toughness is selected. In many embodiments, the content of the main metal or other metals in the alloy is next increased at the expense of the content of one or more of the other composition elements until the GFA of the alloy reaches approximately 1 mm or less, or similarly approaches the minimum GFA that can be printed in a specific additive manufacturing printer. In many embodiments, the alloy&#39;s composition is next adjusted per the toughness test results for the corresponding additively manufactured bulk amorphous part with overall thickness of more than 1 mm. In many such embodiments, following the toughness testing of the bulk part, the alloy&#39;s dominant metal content is either further increased to enhance the part&#39;s toughness (until the alloy can no longer be printed sufficiently amorphous), or decreased to enhance the glass forming ability (and, consequently, the amount of the amorphous phase). 
     Forming the alloys in accordance with embodiments may be done in situ in the melt, or ex situ, where the metallic glass forming alloy is combined with a crystalline phase to form a composite which when deposited alters the fracture toughness of the bulk amorphous metal part as compared to a bulk amorphous metal part formed using a fully amorphous metallic glass forming alloy. In some such embodiments the metallic glass forming alloy and the crystalline phase may be provided in the form of powders with a size distribution within 10% of each other. In other such embodiments, the metallic glass forming alloy and the crystalline phase have different melting temperatures such that during disposition of the metallic glass forming alloy melts and the crystalline phase at most partially melts. 
     In many embodiments, the objective of such alloy composition selection is fabrication of a net shaped amorphous metal part with toughness that is higher than can be achieved for a nearest possible equivalent cast part. The toughness would presumably be the highest for any BMG with the same elements designed around a particular glass-forming composition. It should be noted that several eutectic compositions may exist in a single alloy. For example, the Cu—Zr binary BMG system has three different compositions where BMGs form. In most other BMG systems, there is one particular glass forming eutectic region, which can be used to form a hypoeutectic composition suitable for printing. Using materials according to embodiments, it is possible to form bulk amorphous parts (e.g., having a thickness of at least 1 mm). 
     Embodiments of Methods for Using Additive Manufacturing 
     In many embodiments, the unique features of additive manufacturing are used to compensate for the poor GFA of the alloys of the application to form parts that are tougher than possible using standard forming methods. Specifically, as explained in the diagram provided in  FIG. 8  and further illustrated in  FIG. 9 , in many embodiments, precaution is taken to ensure that each layer of the 3D printed part is cooled faster than the critical cooling rate (R c ) of the alloy being printed, in order to avoid crystallization and subsequent loss of advantageous BMG properties of the bulk part. Exemplary additive manufacturing process that may be used with embodiments include powder bed fusion, directed energy deposition, electron beam melting, wire-fed melting, fused deposition modeling, thermal spray additive manufacturing, laser foil printing, molten metal printing, ultrasonic additive manufacturing, and drop on demand printing. Since different 3D printing processes have different maximum per layer cooling rates, care should be taken in matching the desired alloy to the 3D printing technique. For example, the cooling rate of thermal spray additive is among the highest ( ˜ 10{circumflex over ( )}6 K/s), followed by laser foil printing ( ˜ 10{circumflex over ( )}5 K/s), powder bed fusion ( ˜ 10{circumflex over ( )}4 K/s) and directed energy deposition ( ˜ 10{circumflex over ( )}3 K/s). In other words, in many embodiments, the optimal additive manufacturing technique/cooling rate is determined by carefully matching the manufacturing techniques capabilities to the GFA abilities of a given alloy composition. However, in many embodiments, the cooling rate for a single layer is above 1,000 K/s. In many such embodiments the thickness of each disposed layer is between 1 to 250 micrometers. In various other embodiments the bulk amorphous metal part formed using such methods has a relative density compared to the solid of at least 99.5%. 
     Importantly, in many embodiments, precaution is taken to avoid or minimize alloy embrittlement due to re-crystallization caused by alloy annealing during layer deposition ( FIGS. 9 , and  10 A- 10 B), and also due to annealing embrittlement of the BMG by changing the glass to a less disordered state, even though it remains a glass. Specifically, despite very fast cooling rates for 3D printed layers, high temperature layer annealing is expected to cause annealing embrittlement or partial crystallization and subsequent brittleness, and, as a result, lower toughness, in the additively manufactured parts ( FIGS. 10A and 10B ), especially as compared to cast parts. Therefore, in many embodiments, precaution is taken to select an amorphous metal alloy with a high enough expected initial toughness, such that a bulk part can be produced with higher toughness than that available via conventional techniques, despite the detrimental effects of layer annealing during manufacturing. In addition, in many embodiments, precaution is taken to avoid prolonged annealing or annealing above the glass transition temperature of the alloy being deposited for long times, since both conditions might also cause formation of crystalline phases, as shown in  FIG. 10B . 
     For example, in many embodiments the additive manufacturing process may be modified to ensure that there is cooling of the underlying layer prior to deposition of the overlaid layer. In various such embodiments the time between deposition of layers is extended, such as, for example, by pausing the deposition between layers to give the underlying layer time to cool. In other embodiments, the rate of heating and deposition may be increased such that the underlying layers spend less time being heated and thus reducing the chance for annealing. In still other embodiments the build plate may be heated to within 10% of the glass transition temperature of the metallic glass alloy build material to prevent large differences in the temperature between the disposed layer and the layer to be disposed. In many such embodiments the method of disposing molten layers of the hypoeutectic metallic glass comprises cooling the layers forming the bulk amorphous metal part (e.g., a part having an overall thickness of at least 1 mm) such that they maintain an amorphous fraction of at least 10% by volume and a density of at least 99.8%. 
       FIG. 11  further demonstrates the need to balance the fragility property of an alloy with its sensitivity towards annealing-induced embrittlement, according to the embodiments of the application. Specifically, it has previously been shown that alloys with a good GFA have a higher fragility or fragility-index than the same family alloys with lower GFA. Furthermore, it is also known that amorphous metal alloys can be made tougher by compositional manipulations to increase their fragility, although at the expense of GFA, which diminishes with increased toughness. Unfortunately, as the alloy fragility increases, so does its propensity for annealing embrittlement, as shown in  FIG. 11 . Therefore, the conventional approach has been to additively manufacture with alloys that are good glass formers to minimize crystallization effects from residual heat build-up during the manufacturing process and accompanying annealing embrittlement, even though the resulting bulk parts are more brittle and lack toughness. However, in contrast, in many embodiments, the methods of the instant application, require exactly the opposite—to 3D print bulk parts with high fragility from hypoeutectic metallic glass alloys with poor GFA. According to such embodiments, the initial estimated toughness of the hypoeutectic alloys composed according to the criteria of the instant application are selected to be sufficiently high to overcome known 3D printing drawbacks, such as possible annealing embrittlement. Therefore, in many embodiments, the higher fragility, contrary to conventional wisdom, will lead to higher toughness for the bulk amorphous metal parts additively manufactured according to the methods of the instant application, which is, in turn, expected to be much greater than the toughness of any equivalent cast versions. As such, the bulk amorphous metal parts additively manufactured from hypoeutectic alloys according to the methods of the instant application are expected to have the highest toughness of any bulk amorphous alloys. 
     In many embodiments, the methods of the application can be configured to rely on any 3D process that works with metallic glasses and can achieve per layer cooling rates that are faster than the critical cooling rate for a given BMG alloy. In many such embodiments, the hypoeutectic metal glass forming alloy to be printed is first melted, deposited in a thin layer, and then cooled faster than the alloys critical cooling rate. In many embodiments, the additive manufacturing technique of choice is one of, (but is not limited to): directed energy deposition, such as LENS, thermal spray additive manufacturing, liquid phase printing, direct metal deposition, powder bed fusion such as SLM or DMLS. Alternatively, in other embodiments the metallic glass forming alloy is consolidated during disposition as an amorphous feedstock material that is amorphous and retains the amorphous character and high toughness after disposition. In many embodiments, the layer deposition is affected by either powder injection into a laser, or wire feed into a laser or an electron beam. 
     In some embodiments, non-melting 3D printing processes may be used to manufacture amorphous bulk parts with a toughness greater than 60 MPa m 1/2  using hypoeutectic glass materials. In such embodiments, the hypoeutectic feedstock material is a pre-formed metallic glass wire, powder, or ribbon already having the pre-requisite toughness of at least 60 MPa m 1/2 , which is retained throughout the manufacturing process. In many embodiments, non-melting 3D printing processes are selected from a group that includes (but is not limited to): cold spray, binder jetting, ultrasonic additive manufacturing, any combination thereof. Any of the above process may be conducted under an inert gas environment to prevent oxidation of the layers. 
     Finally, regardless of the process used, the bulk metallic part thus formed may be anything suitable including gears, strain wave gears, knives, cutting tools, bearings, inserts, fasteners, mechanisms, golf clubs, electronic casings, watches, structural coatings, springs, brackets, spacecraft components, and jewelry. 
     EXEMPLARY EMBODIMENTS 
     The following examples are put forth so as to provide those of ordinary skill in the art with a complete disclosure and description of how to make and use the present invention, and are not intended to limit the scope of what the inventors regard as their invention nor are they intended to represent that the experiments below are all or the only experiments performed. Efforts have been made to ensure accuracy with respect to numbers used (e.g. amounts, temperature, etc.) but some experimental errors and deviations should be accounted for. Unless indicated otherwise, parts are parts by weight, molecular weight is weight average molecular weight, temperature is in degrees Celsius, and pressure is at or near atmospheric. 
     Example 1. Additive Manufacturing of Tough BMG Parts from ZrCuNiAl and Other Alloy Families 
       FIGS. 12 and 13 , along with  FIG. 3B , illustrate the embodiments and methods of the application in detail, using a well-studied ZrCuNiAl amorphous metal glass family as an example. First, as follows from the table in  FIG. 3B , compositions with 65 atomic percent of the main metal Zr, i.e. Zr 65 (CuNiAl) 35 , are, in general, good glass formers of the family, all with critical rod diameters greater than 1 mm, and even reaching as high as 10 mm or more for the eutectic compositions. In contrast, hypoeutectic Zr 70 (CuNiAl) 30  alloys (e.g. Zr 70 Ni 16 Cu 6 Al 8  in  FIG. 3B ) demonstrate poorer glass forming abilities (d c   ˜ 5 mm), which are expected to degrade further with increasing Zr content in the composition, to an estimated d c  of  ˜ 1 mm for Zr 75-80 (CuNiAl) 25-20  ( FIG. 12 , top plot). However, increasing Zr content will also increase alloy&#39;s fragility and toughness ( FIG. 12 ). In turn, increased fragility worsens the alloys&#39; sensitivity to annealing embrittlement during 3D printing. Therefore, in many embodiments, a hypoeutectic alloy, such as Zr 70 (CuNiAl) 30  or Zr 80 (CuNiAl) 20  or an even higher Zr-content alloy, wherein the alloy is just a barely good enough glass former to be made amorphous by a fast cooling 3D printing process, is selected for manufacturing of a bulk amorphous metal part according to the methods of the application. In summary, using embodiments it is possible to select alloys for 3D printing that are too fragile (i.e., sensitive to annealing embrittlement) for other forming techniques, such as casting, by allowing the deposited layers to cool prior to further deposition, thereby decoupling the annealing from fragility. Accordingly, such bulk parts of the application are expected to demonstrate toughness that is higher than the toughness of their cast equivalents ( FIG. 12 ). In many embodiments the benchmark for the minimal toughness to be obtained from the alloy composition manipulations according to the methods of the application is 60 MPa m 1/2 . 
       FIG. 13  further details the methods of the instant application using the ZrCuNiAl alloy family as an example. Specifically, in many embodiments, the alloy selection process begins with identification of the eutectic or near-eutectic composition of the alloy family, such that the composition is a known good glass former that can be cast amorphous in a thickness greater than 1 mm. Such good glass former alloys typically have lower fragility and are more brittle. An example of such an alloy composition in the ZrCuNiAl family is Zr 65 Cu 17.5 Ni 10 Al 7.5 , which is a good glass former with a d c  of &gt;6 mm and is of moderate toughness. 
     Next, in many embodiments, the main metal content (Zr in this example) is increased at the cost of the sum of the remaining elements (Cu—Ni—Al, in this example), leading to a hypoeutectic alloy and a weaker glass former composition (d c &lt;5 mm for Zr 70 Cu 6 Ni 16 Al 8 ,  FIG. 3B ), but increased fragility and, therefore, enhanced toughness. Next, in many embodiments, the chosen alloy composition is used in an additive manufacturing process, selected to ensure that each layer is deposited in a thickness of less than 250 microns and is cooled fast enough to produce amorphous material layers, to produce a bulk amorphous metal part with enhanced toughness. Furthermore, in many embodiments, the main metal (e.g. Zr) content is, next, incrementally and iteratively increased within the alloy&#39;s composition until the glass formation ability is so low (&lt;1 mm), that it cannot be compensated for by any available additive manufacturing technique&#39;s cooling rate. Accordingly, the bulk amorphous part produced from the ZrCuNiAl alloy composition optimized for toughness according to the methods of this application is expected to be tougher than any part cast from (good glass former) alloys of this family. As such, all of the metallic glass alloy compositions that can be described by formula Zr 70-95  (Cu—Ni—Al—X) 5-30 , wherein X is any metal or non-metal (e.g., metalloid) element that has a composition contribution of less than 10%, are expected to yield bulk amorphous parts of superior toughness when used according to the methods of the instant application. 
     Similarly, as another example, Zr—Cu family of alloys presented in the table in  FIG. 14A  can also be used according to the methods of this application to produce bulk metallic glass parts of enhanced toughness. In this alloy family, there is a significant content of two metals (Zr and Cu), both of which can be advantageously manipulated. Therefore, according to the application method instructions provided above, as guided by the table in  FIG. 14A  data, all of the metallic glass alloy compositions that can be described by the formula Zr 62-90 Cu 10-23 X 0-28 , wherein X is any one or more elements, including, but not limited to: Nb, Pd, Al, Ti, Fe, Ag, Co, or any combination thereof, are expected to yield bulk amorphous parts of superior toughness when used according to the methods of the instant application. 
     As yet another example, Pt families of the alloys presented in the table in  FIG. 14B  can also be used according to the methods of this application to produce bulk metallic glass parts with enhanced toughness. In these alloy families, the composition content of the main metal Pt must be increased to form a hypoeutectic material in order to improve the alloys&#39; toughness. Therefore, according to the application method instructions provided above, as guided by the data from the table in  FIG. 14B , all of the metallic glass alloy compositions that can be described by formulas Pt 75-95 CO 1-20 X 0-24  and Pt 75-95 P 1-20 X 0-24 , wherein X is any one or more elements, including, but not limited to: P, B, Si, Ni, Ag, Co, or any combination thereof, are expected to yield bulk amorphous parts of superior toughness when used according to the methods of the instant application. Similarly, all of the following alloy compositions presented in  FIGS. 14C through 14I  are suitable for use according to the methods of this application to produce bulk metallic glass parts with enhanced toughness: Pt 56-70 SiBX (based on  FIG. 14C ), Pd &gt;79 PX, ( FIG. 14D ), Cu &gt;60 ZrX ( FIG. 14E ), Ni 75-95 BX and Ni 75-95 PX ( FIG. 14F ), Fe 80-95 PX and Fe 80-95 BX ( FIGS. 14G and 14H , wherein Fe-based alloys have the additional benefits of low cost and inherent high strength), Ti 53-80 ZrX and Ti 53-80 CuX ( FIGS. 14I-1 &amp; 14I-2 ). 
     Example 2. Improving Toughness of Additively Manufactured Zr-Based BMG Parts 
     Bulk amorphous parts have been previously successfully manufactured via 3D printing from the eutectic alloy Zr 52.5 Ti 5 Cu 17.9 Ni 14.6 Al 10  (also known as alloy LM105), which is an excellent glass former. In addition, parts have also been made from the same LM105 alloy via casting, wherein the reported toughness of such cast parts varies from 20-50 MPa m 1/2 . Furthermore, compression tests with the 3D printed parts (shown in  FIG. 15 ) proved that such parts are actually more brittle (have no plasticity) than the equivalent cast parts, despite being printed at a rapid cooling rate, which should have increased the toughness. This is due to the increased oxygen content in the printed alloy and the porosity in the sample. Here, choosing to 3D print bulk amorphous metal parts from alloys of the same Zr-based family, but selected according to the methods of the application to feature increased Zr content, should result in increased fragility and G, and, therefore, much enhanced toughness. 
     Example 3. Improving Toughness of Additively Manufactured Fe-based BMG Parts 
     Similarly to Example 2 discussed above, bulk amorphous parts have been previously successfully manufactured via 3D printing using selective laser melting from eutectic Zr-based and Fe-based alloys. (See, e.g., Mahbooba, et al.,  Applied Materials Today,  11 (2018), p 1-6; and Bordeenithikasem, et al.,  Additive Manufacturing,  21 (2018), p 312-317, the disclosures of which are incorporated herein by reference.) These alloys are good glass formers with critical casting thickness of 3 and 4 mm respectively. Furthermore, these examples also show that the alloy with the 74 atomic percent content of Fe has a low notch toughness of 53 MPa m 1/2  in a cast rod. Although the toughness of the 3D printed parts is not provided, they are expected to be much less tough than their cast equivalents. However, choosing to 3D print bulk amorphous metal parts from alloys of the same Fe-based family, but selected according to the methods of the application to feature increased Fe content (to the point wherein the alloy&#39;s glass forming is reduced to  ˜ 1 mm), should result in parts with much enhanced toughness. 
     DOCTRINE OF EQUIVALENTS 
     This description of the invention has been presented for the purposes of illustration and description. It is not intended to be exhaustive or to limit the invention to the precise form described, and many modifications and variations are possible in light of the teaching above. The embodiments were chosen and described in order to best explain the principles of the invention and its practical applications. This description will enable others skilled in the art to best utilize and practice the invention in various embodiments and with various modifications as are suited to a particular use. The scope of the invention is defined by the following claims.