JP5934366B2 - Molding and separation of bulk solidified amorphous alloys and composites containing amorphous alloys. - Google Patents

Description

  The present invention relates to forming and separating bulk solidified amorphous alloys and composite materials containing amorphous alloys for the production of bulk solidified amorphous alloys, and methods for their production.

  Most metal alloys used today are processed by solidification casting, at least in the early stages. The metal alloy is melted and poured into a metal or ceramic mold where it solidifies. The mold is removed and the cast metal piece can be used as it is or for further processing. The as-cast structure of most materials created during solidification and cooling depends on the cooling rate. There are no general rules regarding the nature of the mutation, but for the most part its structure only changes gradually with changes in cooling rate. On the other hand, for bulk-solidifying amorphous alloys, the change between the amorphous state created by relatively rapid cooling and the crystalline state created by relatively slow cooling is a type change, not a degree, and The two states have distinctly different characteristics.

  In conventional methods for making bulk metallic glass (BMG) parts, a material block is cast in a mold above the melting temperature of the amorphous metal alloy, and the molten amorphous metal alloy is solidified in the mold. It is necessary to form the casting block and then use the cutting tool to remove the gate portion of the casting block and shape the casting block to the desired final shape. However, casting requires a process of melting and cooling the amorphous metal alloy, which prevents the amorphous nature of the BMG component from being controlled. In addition, the cost of subsequent processing to remove the gate and overflowing runners and shape the casting block into the desired final part can be quite expensive. Therefore, new methods for making BMG parts that overcome the limitations of the casting process described above are desired.

  Embodiments herein relate to a high temperature forming and high temperature separation process for bulk solidified amorphous alloys, the process being performed in the supercooled liquid region or near the glass transition temperature.

  Embodiments herein relate to the process of combining BMG alloy casting / forming into a BMG part in a unitary operation without cooling the BMG part to room temperature or near room temperature, whereas conventional processes include: A process of casting / molding a BMG alloy to form a BMG part, a process of cooling the BMG part to near room temperature, and a subsequent process of the BMG part are required.

  One embodiment herein involves melting a BMG material and cutting a portion of the molded BMG part using a hot knife without cooling the molded BMG part to room temperature. Not related to injection molding system. This embodiment relates to the casting of a BMG part at a temperature in the supercooled liquid region of the BMG material in the TTT diagram and the gate removal of the part at that temperature. For example, within the supercooled liquid region of the TMG diagram of the BMG material, the BMG material at a temperature of Tg to Tx is heated to a temperature at which the BMG material can flow, and pressure is applied to the heated flowable BMG material. The mold can be filled with this flowable BMG material, and then a part having the desired final shape can be formed directly in the mold. Therefore, instead of casting the amorphous alloy, the amorphous alloy is formed at a temperature in the supercooled liquid region of the amorphous alloy.

  Another embodiment uses a casting machine or molding machine to cast or mold a BMG part at or near the melting temperature of the BMG material, and cool the BMG material to a temperature below Tg to produce a BMG part. And then using a hot knife to cut the gate and remove the gate and runner from the BMG part at a temperature in the supercooled liquid region of the BMG material in the TTT diagram. This embodiment waits for the molded part to come to room temperature and then uses a conventional tool such as a saw or water jet to remove the gate and runner from the molded part, rather than a temperature between Tg and Tx. The present invention relates to the use of a cutting tool that can be heated up to and incorporating the cutting tool into the mold of the molding system to cut off excess portions of the gate, runners and other molded parts immediately after molding. For example, a typical BMG alloy has a temperature higher than the melting temperature and heats the BMG alloy to about 1100 ° C., injects the molten BMG alloy into a mold, and the molten BMG alloy is about 300-350 ° C. in the mold. Cool to room temperature to form BMG part and cast by shearing part of BMG part (eg gate and runner) using hot knife embedded in mold heated to about 450 ° C be able to. In this way, energy savings and improved process speeds can be achieved by combining the process of casting or molding the BMG part and the subsequent process of partial cutting of the BMG part without cooling the BMG part to room temperature. However, improved cutting can be achieved by shearing the BMG part using a hot knife.

Figure 2 shows a temperature-viscosity diagram for an exemplary bulk solidified amorphous alloy.

FIG. 2 shows a schematic of a time-temperature-transformation (TTT) diagram for an exemplary bulk solidified amorphous alloy.

FIG. 3 shows a schematic diagram of different exemplary embodiments of a forming and casting system. The bulk amorphous alloy has a critical thickness of (a) and the final part has a minimum dimension (> a) that is thicker than its critical thickness. The cutting tool, the bulk amorphous alloy or composite material containing the amorphous alloy, and the mold are heated in some way to near the transition temperature or into the supercooled liquid region. FIG. 3 shows a schematic diagram of different exemplary embodiments of a forming and casting system. The bulk amorphous alloy has a critical thickness of (a) and the final part has a minimum dimension (> a) that is thicker than its critical thickness. The cutting tool, the bulk amorphous alloy or composite material containing the amorphous alloy, and the mold are heated in some way to near the transition temperature or into the supercooled liquid region.

FIG. 6 shows a schematic diagram of microstructure formation on the surface of a BMG part during cutting of the BMG part of another exemplary embodiment. FIG. 6 shows a schematic diagram of microstructure formation on the surface of a BMG part during cutting of the BMG part of another exemplary embodiment.

  All publications, patents, and patent applications cited herein are hereby incorporated by reference in their entirety.

  The articles “a” and “an” are used herein to refer to one or more (ie, at least one) grammatical objects of the article. By way of example, “a polymer resin” means one polymer resin or more than one polymer resin. Any ranges set forth herein are inclusive. As used throughout this specification, the terms “substantially” and “about” are used to describe and explain minor variations. For example, the terms are ± 2% or less, ± 1% or less, ± 0.5% or less, ± 0.2% or less, ± 0.1% or less, ± 0.05% or less, etc. Of ± 5% or less.

  Bulk solidified amorphous alloys, or bulk metallic glass (“BMG”), is a recently developed class of metallic materials. These alloys can be solidified and cooled at a relatively moderate rate, and they maintain an amorphous, amorphous (ie, vitreous) state at room temperature. Amorphous alloys have many superior properties than their crystalline counterparts. However, if the cooling rate is not sufficiently high, crystals may form within the alloy during cooling, and so the benefits of the amorphous state may be lost. For example, one important issue associated with the fabrication of bulk amorphous alloy parts is the partial crystallization of those parts, either by slow cooling or by impurities in the alloy raw materials. Within a BMG part, a high degree of amorphization (and conversely a low degree of crystallinity) is desirable, so a method for casting BMG parts with a controlled amount of amorphization needs to be developed. There is sex.

  FIG. 1 (obtained from US Pat. No. 7,575,040) is an exemplary bulk from the VIT-001 series of the Zr--Ti--Ni--Cu--Be family manufactured by Liquidmetal Technology. The viscosity-temperature graph of a solidified amorphous alloy is shown. It should be noted that there is no clear liquid / solid transformation for bulk solidifying amorphous metals during the formation of amorphous solids. This molten alloy becomes increasingly viscous with increasing supercooling until it approaches a solid form near the glass transition temperature. Thus, the temperature of the solidification front for the bulk solidified amorphous alloy can be near the glass transition temperature, at which point the alloy effectively acts as a solid for the purpose of drawing the quenched amorphous sheet product.

  FIG. 2 (obtained from US Pat. No. 7,575,040) shows a time-temperature-transformation (TTT) cooling curve, or TTT diagram, of an exemplary bulk solidified amorphous alloy. Bulk solidified amorphous metals, like conventional metals, do not experience liquid / solid crystallization transformations upon cooling. Instead, highly fluid, amorphous forms of metals found at high temperatures (near the “melting temperature” Tm) become more viscous as the temperature is reduced (to near the glass transition temperature Tg). Finally, it exhibits the external physical properties of conventional solids.

  For bulk solidified amorphous metals, the “melting temperature” Tm can be defined as the thermodynamic liquid phase temperature of the corresponding crystalline phase, even though there is no liquid / crystallization transformation. Under this regime, the viscosity at the melting temperature of the bulk solidified amorphous alloy can range from about 0.1 poise to about 10,000 poise, and in some cases, less than 0.01 poise. . This lower viscosity at the “melting temperature” results in faster and complete filling of complex parts of the shell / mold with bulk solidified amorphous metal to form BMG parts. In addition, the cooling rate of the molten metal to form the BMG part is such that the time-temperature profile during cooling does not cross the nose shaped region that bounds the crystallization region in the TTT diagram of FIG. There must be. In FIG. 2, T nose is the critical crystallization temperature Tx where crystallization is most rapid and occurs on the shortest time scale.

The supercooled liquid region, Tg-Tx temperature region, demonstrates extreme stability against crystallization of the bulk solidified alloy. Within this temperature range, the bulk solidified alloy can exist as a highly viscous liquid. The viscosity of the bulk solidified alloy in this supercooled liquid region ranges from 10 ¹² Pa · s at the glass transition temperature to 10 ⁵ Pa · s at the high temperature limit of the supercooled liquid region, which is the crystallization temperature. Can vary between. A liquid having such a viscosity can experience substantial plastic strain under pressure. Embodiments herein utilize the large plastic formability within this supercooled liquid region as a forming and separating method.

  It is necessary to clarify Tx. Technically, the nose shaped curve shown in the TTT diagram describes Tx as a function of temperature and time. Therefore, Tx is reached when it hits this TTT curve, regardless of the trajectory followed during heating or cooling of the metal alloy. In FIG. 1 (b), Tx is shown as a dashed line because Tx can vary from proximal Tm to proximal Tg.

  The schematic TTT diagram of FIG. 2 shows a die-cast processing method with a time-temperature trajectory (shown as (1) as an exemplary trajectory as (1)) that does not hit the TTT curve and is between Tm and less than Tg. . During die casting, this forming is performed at the same time as substantially rapid cooling to avoid the trajectory hitting the TTT curve. Time-temperature trajectory (shown as exemplary trajectories (2), (3), and (4)) does not hit the TTT curve, and processing related to superplastic forming (SPF) from below Tg to below Tm Processing method. In SPF, amorphous BMG is reheated into the supercooled liquid region, and the available processing window is much larger than die casting, which can result in better process controllability. . The SPF process does not require rapid cooling to avoid crystallization during cooling. Also, as shown by exemplary trajectories (2), (3), and (4), SPF is performed with the highest temperature during SPF being above or below T nose and up to about Tm can do. Although the temperature of one amorphous alloy is raised, when it is managed so as to avoid hitting the TTT curve, Tx is not reached even when heated to “Tg to Tm”.

  The typical differential scanning calorimeter (DSC) heating curve of bulk solidified amorphous alloys, obtained at a heating rate of 20 ° C./min, largely describes the specific trajectory across the TTT data. There will be a Tg at temperature, a Tx where the DSC heating ramp intersects the onset of TTT crystallization, and finally a melting peak where the same trajectory intersects the temperature range for melting. Avoid TTT curves completely when heating bulk solidified amorphous alloys at a rapid heating rate as shown by the up-tilted portions of trajectories (2), (3), and (4) in FIG. And DSC data show a glass transition upon heating but no Tx. Another way of thinking about this is that the trajectories (2), (3), and (4) are within the TTT curve nose (and further above) to the temperature of the Tg line, as long as they do not hit the crystallization curve. It can fit in any place. That simply means that as the processing temperature increases, the horizontal flats in the trajectory can become much shorter.

Phase As used herein, the term “phase” can refer to what can be found in a thermodynamic phase diagram. A phase is a region of space (eg, a thermodynamic system) throughout which all physical properties of the material are essentially uniform. Examples of physical properties include density, refractive index, chemical composition, and lattice periodicity. A simple description of a phase is a region of material that is chemically uniform, physically distinct, and / or mechanically separable. For example, in a system consisting of ice and water in a glass jar, the ice cube is one phase, water is the second phase, and humid air above the water is the third phase. Jar glass is another separate phase. A phase can refer to a solid solution that can be a two-component, three-component, four-component or higher solution or compound, such as an intermetallic compound. As another example, the amorphous phase is completely different from the crystalline phase.

Metals, transition metals, and non-metals The term “metal” refers to an electropositive chemical element. As used herein, the term “element” generally refers to an element that can be found in the periodic table. Physically, a ground state metal atom includes a partially filled band with an empty state close to the occupied state. The term “transition metal” is the third in the periodic table that has an incomplete internal electron shell and serves as a transition link between the most electropositive and the least electropositive in a set of elements. It is one of the metal elements within the range of Group 12 to Group 12. Transition metals are characterized by multiple valences, colored compounds, and the ability to form stable complex ions. The term “nonmetal” refers to a chemical element that does not have the ability to lose electrons and form a cation.

  Depending on the application, any suitable non-metallic elements, or combinations thereof, can be used. An alloy (or “alloy composition”) may include a plurality of non-metallic elements, such as at least two, at least three, at least four or more non-metallic elements. The nonmetallic element can be any element found within Groups 13-17 in the periodic table. For example, the nonmetallic elements are F, Cl, Br, I, At, O, S, Se, Te, Po, N, P, As, Sb, Bi, C, Si, Ge, Sn, Pb, and B. It can be any one of them. In some cases, the non-metallic element can refer to a specific metalloid within Group 13 to Group 17 (eg, B, Si, Ge, As, Sb, Te, and Po). In one embodiment, the non-metallic element can include B, Si, C, P, or a combination thereof. Thus, for example, the alloy can include borides or carbides, or both.

  Transition metal elements are scandium, titanium, vanadium, chromium, manganese, iron, cobalt, nickel, copper, zinc, yttrium, zirconium, niobium, molybdenum, technetium, ruthenium, rhodium, palladium, silver, cadmium, hafnium, tantalum, tungsten , Rhenium, osmium, iridium, platinum, gold, mercury, rutherfordium, dobnium, seaborgium, bolium, hassium, mitonium, ununnilium, ununnium, and ununbium. In one embodiment, the transition metal element-containing BMG is Sc, Y, La, Ac, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Mn, Tc, Re, Fe, Ru, Os, It may have at least one of Co, Rh, Ir, Ni, Pd, Pt, Cu, Ag, Au, Zn, Cd, and Hg. Depending on the application, any suitable transition metal element, or combinations thereof, can be used. The alloy composition may include a plurality of transition metal elements, such as at least 2, at least 3, at least 4 or more transition metal elements.

  An alloy or alloy “sample” or “specimen” alloy described herein may have any shape or size. For example, the alloy can have a particulate shape, which can have a shape such as a sphere, ellipse, wire, rod, sheet, flake, or irregular shape. The microparticles can have any size. For example, the microparticles can be about 5 micrometers to about 80 micrometers, such as about 10 micrometers to about 60 micrometers, such as about 15 micrometers to about 50 micrometers, such as about 15 micrometers to about 45 micrometers, etc. It may have an average diameter of about 1 micrometer to about 100 micrometers, such as about 25 micrometers to about 35 micrometers, such as about 20 micrometers to about 40 micrometers. For example, in one embodiment, the average diameter of the microparticles is from about 25 micrometers to about 44 micrometers. In some embodiments, smaller particles, such as those in the nanometer range, or larger particles, such as those larger than 100 micrometers, can be used.

  The alloy sample or specimen can also be of much larger dimensions. For example, it can be a bulk structural component such as an ingot, an electronics enclosure / casing, or even a portion of a structural component having dimensions in the millimeter, centimeter, or meter range.

Solid solution The term “solid solution” refers to a solid form of a solution. The term “solution” refers to a mixture of two or more substances that can be a solid, liquid, gas, or a combination thereof. This mixture can be homogeneous or heterogeneous. The term “mixture” is a composition of two or more substances that can be combined with each other and generally separated. In general, the two or more substances are not combined with each other.

Alloys In some embodiments, the alloy compositions described herein can be fully alloyed. In one embodiment, an “alloy” refers to a homogenous mixture or solid solution of two or more metals in which one atom replaces another atom or occupies an interstitial position between atoms. For example, brass is an alloy that is an alloy of zinc and copper, as opposed to a composite material, which is partially or completely of one or more elements in a metal matrix, such as one or more compounds in the metal matrix. A solid solution. The term alloy herein may refer to both a fully solid solution alloy that may exhibit a single solid phase microstructure and a partial solution that may exhibit two or more phases. The alloy compositions described herein can refer to those comprising an alloy or those comprising an alloy-containing composite material.

  Thus, a fully alloyed alloy can have a homogeneous distribution of its constituents, whether in solid solution phase, compound phase, or both. As used herein, the term “fully alloyed” can describe slight variations within tolerances. For example, the term includes at least 90% alloying, such as at least 95% alloying, such as at least 99% alloying, such as at least 99.5% alloying, such as at least 99.9% alloying. Can point. Percentages herein can refer to either volume percentages or weight percentages, depending on the context. These percentages can be balanced by impurities, which can be in terms of compositions or phases that are not part of the alloy.

Amorphous or Amorphous Solid An “amorphous” or “amorphous solid” is a solid that lacks the lattice periodicity characteristic of crystals. As used herein, “amorphous solid” includes “glass”, which is an amorphous solid that softens and transforms into a liquid state upon heating through the glass transition. In general, amorphous materials lack the long-range order characteristic of crystals, but these amorphous materials can possess some short-range order on the atomic length scale due to the nature of chemical bonds. A distinction between an amorphous solid and a crystalline solid can be made based on lattice periodicity determined by structural property evaluation techniques such as X-ray diffraction and transmission electron microscopy.

  The terms “order” and “disorder” indicate the presence or absence of any symmetry or correlation within a multiparticulate system. The terms “long-range order” and “short-range order” distinguish order within a material based on a length scale.

  The most exact form of order in a solid is lattice periodicity. A specific pattern (the arrangement of atoms in the unit cell) is repeated many times to form a translationally invariant, space filling. This lattice periodicity is a defining characteristic of crystals. The possible symmetries are grouped into 14 Bravey lattices and 230 space groups.

  Lattice periodicity suggests long-range order. If only one unit cell is known, its translational symmetry makes it possible to accurately predict all atomic arrangements at an arbitrary distance. The converse is generally true, except in the case of, for example, quasicrystals that have a completely deterministic filling but do not possess lattice periodicity.

Long-range order characterizes a physical system in which remote parts of the same sample exhibit correlated behavior. This long-range order can be expressed as a correlation function, that is, the next spin-spin correlation function.

  In the above function, s is a spin quantum number and x is a distance function in a specific system. This function is equal to the identity element when x = x ′ and decreases as the distance | x−x ′ | Typically, this function decays exponentially to zero over long distances and the system is considered disordered. However, if this correlation function decays to a constant value with a large | x−x ′ |, it can be stated that the system possesses long-range order. If this function decays to zero as a power of distance, it can be called quasi-long-range order. Note that what constitutes a large value of | x-x '| is relative.

  A system can be extended by presenting a quenching disorder, eg, spin glass, if some of the parameters that define its behavior are random variables that do not evolve over time (ie, they are quenched or frozen). it can. This quenching disorder is the opposite of the annealing disorder in which the random variable itself can develop. Embodiments herein include systems that include a quenching disorder.

  The alloys described herein can be crystalline, partially crystalline, amorphous, or substantially amorphous. For example, an alloy sample / specimen may include at least some degree of crystallinity, with the grains / crystals having a size in the nanometer and / or micrometer range. Alternatively, the alloy can be substantially amorphous, such as sufficiently amorphous. In one embodiment, the alloy composition is not at least substantially amorphous, such as substantially crystalline, such as fully crystalline.

  In one embodiment, the presence of one or more crystals in another amorphous alloy can be interpreted as a “crystalline phase” in that alloy. The degree of crystallinity of an alloy (or in some embodiments, “crystallinity” for short) can refer to the amount of crystalline phase present in the alloy. The degree can refer, for example, to the fraction of crystals present in the alloy. This fraction can refer to a volume fraction or a weight fraction, depending on the context. A measure of how “amorphous” an amorphous alloy can be is the degree of amorphization. The degree of amorphization can be measured from the viewpoint of the degree of crystallinity. For example, in one embodiment, an alloy having a low degree of crystallinity can be described as having a high degree of amorphousness. In one embodiment, for example, an alloy having 60% by volume crystalline phase may have 40% by volume amorphous phase.

Amorphous alloy or amorphous metal "Amorphous alloy" means an amorphous content of more than 50% by volume, preferably more than 90% by volume, more preferably more than 95% by volume, most preferably 99% by volume. An alloy having an amorphous content of from super to almost 100% by volume. As noted above, it should be noted that alloys with a high degree of amorphization have an equally low degree of crystallinity. An “amorphous metal” is an amorphous metal material having a disordered atomic scale structure. By being crystalline, amorphous alloys are amorphous, as opposed to most metals, which have a highly ordered atomic arrangement. The material in which such a disordered structure is created directly from the liquid state during cooling may be referred to as “glass”. Thus, amorphous metals are commonly referred to as “metallic glass” or “glass metal”. In one embodiment, bulk metallic glass (“BMG”) can refer to an alloy whose microstructure is at least partially amorphous. However, in addition to extreme rapid cooling, there are several ways to create amorphous metals, including physical vapor deposition, solid phase reaction, ion irradiation, melt spinning, and mechanical alloying. Amorphous alloys can be a single class of materials regardless of how they are prepared.

  Amorphous metal can be produced through various quenching methods. For example, amorphous metal can be created by sputtering molten metal onto a rotating metal disk. A quench of about several million degrees per second can be too fast for crystals to form, so that the metal is “fixed” in the glassy state. Amorphous metals / alloys can also be created with critical cooling rates that are slow enough to allow the formation of thick layer amorphous structures, such as bulk metallic glass.

  The terms “bulk metallic glass” (“BMG”), bulk amorphous alloy (“BAA”), and bulk solidified amorphous alloy are used interchangeably herein. These terms refer to an amorphous alloy having a minimum dimension in the range of at least millimeters. For example, the dimension is at least about 0, such as at least about 1 mm, at least about 2 mm, at least about 4 mm, at least about 5 mm, at least about 6 mm, at least about 8 mm, at least about 10 mm, at least about 12 mm, etc. .5 mm. Depending on the geometry, the dimensions can refer to diameter, radius, thickness, width, length, etc. The BMG may also be a metallic glass having at least one dimension in the centimeter range, such as at least about 1.0 cm, such as at least about 2.0 cm, such as at least about 5.0 cm, such as at least about 10.0 cm. You can also. In some embodiments, the BMG may have at least one dimension in the range of at least meters. BMG can exhibit any of the shapes or forms described above with respect to metallic glass. Accordingly, the BMG described herein may differ from thin films made by conventional deposition techniques in one important aspect in some embodiments, the former BMG being the latter The size can be much larger than that of the thin film.

  The amorphous metal can be an alloy rather than a pure metal. This alloy can contain atoms of significantly different sizes, resulting in a low free volume in the molten state (and therefore has a viscosity that is orders of magnitude higher than other metals and alloys). . This viscosity prevents atoms from moving sufficiently to form an ordered lattice. This material structure can provide low shrinkage during cooling and resistance to plastic deformation. This absence of grain boundaries, which in some cases is a weakness of crystalline materials, can result in better resistance to wear and corrosion, for example. In one embodiment, although technically glass, amorphous metals can also be much stronger and less brittle than oxide glasses and ceramics.

  The thermal conductivity of amorphous materials can be lower than the thermal conductivity of their crystalline counterparts. In order to achieve the formation of an amorphous structure even during slower cooling, an alloy is made with three or more components, resulting in a composite crystal unit with higher potential energy and lower probability of formation. be able to. The formation of an amorphous alloy depends on several factors: the composition of the alloy components and the atomic radii of the components (preferably greater than 12% in order to achieve high packing density and low free volume). And the negative heat of mixing of the combination of components that prevents crystal nucleation and extends the time that the molten metal remains supercooled. However, since the formation of an amorphous alloy is based on a wide variety of variables, it may be difficult to determine in advance whether the alloy composition forms an amorphous alloy.

  For example, amorphous alloys of boron, silicon, phosphorus, and other glass formers with magnetic metals (iron, cobalt, nickel) can be magnetic with low coercivity and high electrical resistance. This high resistance results in a low loss due to eddy currents when exposed to an alternating magnetic field, which is a characteristic useful as, for example, a transformer core.

  Amorphous alloys can have a variety of properties that are potentially useful. Specifically, amorphous alloys tend to be stronger than crystalline alloys of similar chemical composition, and they can withstand greater reversible ("elastic") deformation than crystalline alloys. Amorphous metals derive their strength directly from their amorphous structure, which can have no defects (such as dislocations) that limit the strength of the crystalline alloy. For example, one state-of-the-art amorphous metal, known as Vitreloy ™, has a tensile strength approximately twice that of high-grade titanium. In some embodiments, the metallic glass at room temperature is not ductile and breaks suddenly when tension is applied, which is not evident in imminent failure, so in applications where reliability is important, Limit applicability of the material. Therefore, to overcome this challenge, metal matrix composites with a metallic glass matrix containing ductile crystalline metal dendritic particles or fibers can be used. Alternatively, BMG with less elements (eg, Ni) that tend to cause seriousness can be used. For example, by using BMG that does not contain Ni, the ductility of the BMG can be improved.

  Another useful property of bulk amorphous alloys is that they can be intrinsic glasses, in other words, bulk amorphous alloys can soften and flow when heated. This allows easy processing, such as by injection molding, in much the same way as a polymer. As a result, amorphous alloys can be used to make sports equipment, medical devices, electronic components and equipment, and thin films. Amorphous metal thin films can be deposited as protective coatings via high speed oxygen fuel technology.

  The material can have an amorphous phase, a crystalline phase, or both. These amorphous and crystalline phases can have the same chemical composition and differ only in microstructure (ie, one is amorphous and the other is crystalline). Microstructure in one embodiment refers to the structure of the material as revealed by a microscope with a magnification of 25X or higher. Alternatively, these two phases can have different chemical compositions and microstructures. For example, the composition can be partially amorphous, substantially amorphous, or fully amorphous.

  As described above, the degree of amorphization (and conversely the degree of crystallinity) can be measured by the fraction of crystals present in the alloy. The degree can refer to the volume fraction or weight fraction of the crystalline phase present in the alloy. A partially amorphous composition includes at least about 10%, such as at least about 20%, such as at least about 40%, such as at least about 60%, such as at least about 80%, such as at least about 90%. , Which can refer to a composition at least about 5% by volume of which is in an amorphous phase. The terms “substantially” and “about” are defined elsewhere in this specification. Thus, a composition that is at least substantially amorphous includes at least about 99.8 vol%, such as at least about 95 vol%, such as at least about 98 vol%, such as at least about 99 vol%, such as at least about 99.5 vol%. %, Such as at least about 99.9% by volume, at least about 90% by volume of which is amorphous. In one embodiment, the substantially amorphous composition can have any attendant minor crystalline phase present therein.

  In one embodiment, the amorphous alloy composition can be homogeneous with respect to the amorphous phase. A substance with a uniform composition is homogeneous. This is in contrast to materials that are heterogeneous. The term “composition” refers to the chemical composition and / or microstructure in a substance. A substance is homogeneous when the volume of the substance is divided in half and both halves have substantially the same composition. For example, a particulate suspension is homogeneous when the volume of the particulate suspension is divided in half and both halves have substantially the same volume of particles. However, it may be possible to see individual particles under a microscope. Another example of a homogeneous material is air, where the various components in the air are equally suspended, but particles, gases, and liquids in the air can be analyzed separately or separated from the air. You can also.

  A composition that is homogeneous with respect to an amorphous alloy can refer to one having an amorphous phase that is distributed substantially uniformly throughout its microstructure. In other words, the composition macroscopically comprises an amorphous alloy that is distributed substantially uniformly throughout the composition. In an alternative embodiment, the composition can be of a composite material having an amorphous phase with a non-amorphous phase therein. This non-amorphous phase can be a single crystal or multiple crystals. The crystals can be in the form of particulates of any shape, such as spherical, oval, wire, rod, sheet, flake, or irregular shape. In one embodiment, the crystals can have a dendritic morphology. For example, an at least partially amorphous composite composition may have a crystalline phase in the form of dendrites dispersed in an amorphous phase matrix, and this dispersion may be uniform or non-uniform. In one embodiment, the amorphous phase and the crystalline phase can have the same chemical composition or different chemical compositions, and the phases can have substantially the same chemical composition. In another embodiment, the crystalline phase can be more ductile than the BMG phase.

  The methods described herein may be applicable to any type of amorphous alloy. Similarly, the amorphous alloy described herein as a component of the composition or article can be of any type. The amorphous alloy may include elements of Zr, Hf, Ti, Cu, Ni, Pt, Pd, Fe, Mg, Au, La, Ag, Al, Mo, Nb, Be, or combinations thereof. That is, the alloy may include any combination of these elements in its chemical formula or chemical composition. These elements can be present in various weight or volume percentages. For example, an iron “base” alloy can refer to an alloy having a non-negligible weight percentage of iron present therein, the weight percentage being at least about 40% by weight, for example, at least about 40% by weight. It may be at least about 20%, such as 50%, such as at least about 60%, such as at least about 80%. Alternatively, in one embodiment, the percentages described above can be volume percentages instead of weight percentages. Thus, the amorphous alloy can be a zirconium base, a titanium base, a platinum base, a palladium base, a gold base, a silver base, a copper base, an iron base, a nickel base, an aluminum base, a molybdenum base, and the like. The alloy may also not include any of the above-described elements to suit a particular purpose. For example, in some embodiments, the alloy, or a composition comprising the alloy, can be substantially free of nickel, aluminum, titanium, beryllium, or combinations thereof. In one embodiment, the alloy or composite material does not include any nickel, aluminum, titanium, beryllium, or combinations thereof.

For example, the amorphous alloy may have the formula (Zr, Ti) _a (Ni, Cu, Fe) _b (Be, A1, Si, B) _c , where a, b, and c are Each represents a weight percentage or an atomic percentage. In one embodiment, in atomic percent, a is in the range of 30-75, b is in the range of 5-60, and c is in the range of 0-50. Alternatively, the amorphous alloy can have the formula (Zr, Ti) _a (Ni, Cu) _b (Be) _c , where a, b, and c are weight percentages or atomic percentages, respectively. Represent. In one embodiment, in atomic percent, a is in the range of 40-75, b is in the range of 5-50, and c is in the range of 5-50. The alloy may also have the formula (Zr, Ti) _a (Ni, Cu) _b (Be) _c , where a, b, and c represent weight percentage or atomic percentage, respectively. In one embodiment, in atomic percent, a is in the range of 45-65, b is in the range of 7.5-35, and c is in the range of 10-37.5. Alternatively, the alloy can also have the formula (Zr) _a (Nb, Ti) _b (Ni, Cu) _c (A1) _d , where a, b, c, and d are each weight Represents a percentage or atomic percentage. In one embodiment, in atomic percent, a is in the range of 45-65, b is in the range of 0-10, c is in the range of 20-40, and d is in the range of 7.5-15. . One exemplary embodiment of the above alloy system is Zr-Ti-Ni- of the trade name Vitreloy (TM), such as Vitreloy-1 and Vitreloy-101, as manufactured by Liquidmetal Technologies (CA, USA). It is a Cu-Be based amorphous alloy. Some examples of various systems of amorphous alloys are listed in Table 1.

These amorphous alloys can also be iron alloys, such as (Fe, Ni, Co) based alloys. Examples of such compositions are described in US Pat. Nos. 6,325,868, 5,288,344, 5,368,659, 5,618,359, and 5,735,975, Inoue et al., Appl. Phys. Lett. , Volume 71, p 464 (1997), Shen et al., Mater. Trans. , JIM, Volume 42, p 2136 (2001), and Japanese Patent Application No. 200126277 (publication number 2001303218 (A)). One exemplary composition is Fe ₇₂ A1 ₅ Ga ₂ P _ll C ₆ B ₄ . Another example is Fe ₇₂ A1 ₇ Zr ₁₀ Mo ₅ W ₂ B ₁₅ . Another iron-based alloy system that can be used for coating herein is disclosed in U.S. Patent Application Publication No. 2010/0084052, the amorphous metal having a composition described in parentheses, for example. Of manganese (1 to 3 atomic%), yttrium (0.1 to 10 atomic%), and silicon (0.3 to 3.1 atomic%), and the composition described in parentheses The following elements in the specified range: Chromium (15-20 atom%), Molybdenum (2-15 atom%) Tungsten (1-3 atom%), Boron (5-16 atom%), Carbon (3-16 atom%) And the balance iron.

The amorphous alloy system described above may further include additional elements, such as additional transition metal elements including Nb, Cr, V, and Co. These additive elements may be present at about 30 wt% or less, such as about 20 wt% or less, such as about 10 wt% or less, such as about 5 wt%. In one embodiment, the optional additive element is at least one of cobalt, manganese, zirconium, tantalum, niobium, tungsten, yttrium, titanium, vanadium, and hafnium, forming carbides and wear resistant. Further improve the properties and corrosion resistance. Further optional elements may include phosphorus, germanium, and arsenic, up to a total of about 2%, preferably less than 1%, to lower the melting point. Other minor impurities should be less than about 2%, preferably less than 0.5%.

  In some embodiments, a composition having an amorphous alloy can include a small amount of impurities. By intentionally adding impurity elements, the properties of the composition, such as improved mechanical properties (eg, hardness, strength, fracture mechanism, etc.) and / or improved corrosion resistance can be modified. Alternatively, the impurities may be present as inevitable incidental impurities, such as those obtained as processing and manufacturing by-products. This impurity is about 10% or less, such as about 5% or less, such as about 2% or less, such as about 1% or less, such as about 0.5% or less, such as about 0.1% or less. can do. In some embodiments, these percentages can be volume percentages instead of weight percentages. In one embodiment, the alloy sample / composition consists essentially of an amorphous alloy (having only a small amount of incidental impurities). In another embodiment, the composition comprises an amorphous alloy (having no observable trace impurities).

  In one embodiment, the final part exceeded the critical cast thickness of the bulk solidified amorphous alloy.

  In embodiments herein, superplastic forming is possible due to the presence of a supercooled liquid region in which the bulk solidified amorphous alloy can exist as a high viscosity liquid. Large plastic deformation can be obtained. The ability to plastically deform significantly in the supercooled liquid region is used for the molding and / or cutting process. In contrast to solids, this liquid bulk solidified alloy deforms locally, which greatly reduces the energy required for cutting and forming. The ease of cutting and forming varies with the temperature of the alloy, mold and cutting tool. As the temperature increases, the viscosity decreases, resulting in easier cutting and molding.

  Embodiments herein can utilize a thermoplastic molding process using amorphous alloys, for example, performed at Tg-Tx. As used herein, Tx and Tg are determined from standard DSC measurements at typical heating rates (eg, 20 ° C./min) as the temperature of onset of crystallization and the temperature of onset of glass transition. .

The amorphous alloy component can have a critical casting thickness, and the final part can have a thickness greater than its critical casting thickness. Furthermore, the time and temperature of the heating and shaping operations are selected such that the elastic strain limit of the amorphous alloy can be substantially maintained at 1.0% or higher, preferably 1.5% or higher. In the context of embodiments herein, the temperature near the glass transition means that the molding temperature can be below the glass transition temperature, near the glass transition temperature or glass transition temperature, and above the glass transition temperature. is preferably a temperature lower than the crystallization temperature T _x. The cooling step is performed at a rate similar to the heating rate in the heating step, preferably at a rate exceeding the heating rate in the heating step. The cooling step is also preferably accomplished while the forming and shaping loads are still maintained.

Electronic Device The embodiments described herein can be valuable in creating an electronic device using BMG. As used herein, an electronic device can refer to any electronic device known in the art. For example, the electronic device can be any communication device such as a phone such as a mobile phone and a landline phone, or a smartphone including, for example, iPhone ™, and an e-mail sending / receiving device. The electronic device can be part of a display, such as a digital display, TV monitor, electronic book reader, portable web browser (eg, iPad ™), and computer monitor. The electronic device can also be an entertainment device including a music player such as a portable DVD player, a conventional DVD player, a Blu-ray disc player, a video game console, a portable music player (eg, iPod ™), and the like. . The electronic device can also be part of a device that provides control (eg, Apple TV ™), such as controlling image, video, audio streaming, or remote control for the electronic device It can be a device. The electronics can be part of a computer or computer accessory such as a hard drive tower enclosure or casing, laptop enclosure, laptop keyboard, laptop trackpad, desktop keyboard, mouse, and speakers. . This article can also be applied to devices such as watches or watches.

Bulk Solidifying Amorphous Alloy Forming / Casting and Separation In one embodiment, the final part exceeded the critical cast thickness of the bulk solidifying amorphous alloy.

  In another embodiment, the hot molding and hot separation can be performed in any order or alone.

  In another embodiment, the bulk solidifying amorphous alloy or composite material containing amorphous alloy, mold, and cutting tool is at the cutting temperature of the supercooled liquid region.

  In yet another embodiment, the bulk solidifying amorphous alloy or composite material containing amorphous alloy, mold, and cutting tool is at the cutting temperature of the supercooled liquid region. A wire is used as a cutting tool.

  In yet another embodiment, the bulk solidifying amorphous alloy or composite material containing amorphous alloy, mold, and cutting tool is at the cutting temperature of the supercooled liquid region. The cutting tool is a blade.

  In yet another embodiment, the bulk solidifying amorphous alloy, mold, and cutting tool are at the cutting temperature of the supercooled liquid region. Cutting is performed by shearing the two surfaces together. A composite material containing a bulk solidified alloy or an amorphous alloy is connected to one surface.

  In yet another embodiment, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is heated locally to the cutting temperature (where the cutting is performed) and the bulk solidified amorphous alloy can be at any temperature. .

  In yet another embodiment, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is heated locally to the cutting temperature (where the cutting is performed) and the bulk solidified amorphous alloy can be at any temperature. . A wire heated to the cutting temperature is used as a cutting tool.

  In yet another embodiment, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is heated locally to the cutting temperature (where the cutting is performed) and the bulk solidified amorphous alloy can be at any temperature. . A plate heated to the cutting temperature is used as a cutting tool.

  In yet another embodiment, the bulk-solidifying amorphous alloy or composite material containing the amorphous alloy is heated locally to the cutting temperature (where the cutting is performed) and the bulk-solidifying amorphous alloy or composite containing the amorphous alloy The material can be at any temperature. Cutting is performed by shearing two heated surfaces together.

  In yet another embodiment, a cut is performed to separate the reservoir containing the ingredients and the part.

  In yet another embodiment, the purpose of cutting is to provide a desirable shape in which a bulk solidified amorphous alloy or a composite material containing an amorphous alloy is molded within a mold cavity.

  In yet another embodiment, the purpose of cutting is to provide a desirable stock material in which a bulk solidified amorphous alloy or a composite material containing an amorphous alloy is molded in a mold cavity.

  In another embodiment, a bulk solidified amorphous alloy or composite material containing an amorphous alloy in the supercooled liquid region is forced into the mold cavity and heated in the supercooled liquid region.

  In another embodiment, a bulk solidified amorphous alloy or composite material containing an amorphous alloy in the supercooled liquid region is forced into the mold cavity and heated to less than the supercooled liquid region.

  In another embodiment, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is laser, resistance furnace or the like, or heated inductively.

  In another embodiment, the mold can also function as a cutting tool.

  In another embodiment, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is heated by a plunger and / or mold in the supercooled liquid region.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Zr / Ti based.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Zr-based.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Zr / Ti based and does not contain Ni.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Zr / Ti based and does not contain Al.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Zr / Ti based and does not contain Be.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Cu-based.

  In one embodiment of the forming and separating method, the provided bulk solidified amorphous alloy is Fe-based.

  In one embodiment of the forming and separating method, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is formed and / or separated into a net-shaped part under reduced pressure.

  In one embodiment of the forming and separating method, the bulk solidified amorphous alloy or the composite material containing the amorphous alloy is formed and / or separated into a net-shaped part under an inert atmosphere.

  In one embodiment of the forming and separating method, the bulk solidified amorphous alloy or composite material containing the amorphous alloy is formed and / or separated into a net-shaped part under partial vacuum.

  In one embodiment of the forming and separating method, the bulk-solidifying amorphous alloy or the composite material containing the amorphous alloy may be formed and / or separated one or more times.

  In embodiments herein, superplastic forming is possible due to the presence of a supercooled liquid region in which the bulk solidified amorphous alloy can exist as a high viscosity liquid. Large plastic deformation can be obtained. The ability to greatly plastically deform in the supercooled liquid region is used for the molding and / or cutting process. In contrast to solids, this liquid bulk solidified alloy deforms locally, which greatly reduces the energy required for cutting and forming. The ease of cutting and forming varies with the temperature of the alloy, mold and cutting tool. As the temperature increases, the viscosity decreases, resulting in easier cutting and molding.

  The cutting and forming process can be performed on samples of uniform temperature at the cutting temperature, where the cutting tool is also at the cutting temperature. However, this is not essential. Alternatively, the sample temperature is variable and is the cutting temperature only locally at the location where the cutting is performed. This can be done by locally heating or by heating the cutting tool or mold. On the other hand, the molding process should be performed on samples that are at a uniform temperature, and the mold can be heated to or below the supercooled liquid region to obtain the desired molding and cooling performance.

  As used herein, Tx and Tg are standard DSC (differential scanning calorimeters) at typical heating rates (eg, 20 ° C./min) as the temperature at the beginning of crystallization and the temperature at the beginning of the glass transition. ) Determined from measurement.

The raw material can have a critical casting thickness and the final part can have a thickness greater than the critical casting thickness. Furthermore, the time and temperature of the heating and shaping operations are selected such that the elastic strain limit of the amorphous alloy is substantially maintained above 1.0%, preferably above 1.5%. In the context of embodiments herein, the temperature near the glass transition means that the molding temperature can be below the glass transition temperature, near the glass transition temperature or glass transition temperature, and above the glass transition temperature. The temperature is preferably _lower than the crystallization temperature T _x . The cooling step is performed at a rate similar to the heating rate in the heating step, preferably at a rate exceeding the heating rate in the heating step. The cooling step is also preferably accomplished while the forming and shaping loads are still maintained.

  In one embodiment, a BMG alloy that is already in the form of an amorphous alloy can be heated from room temperature to a temperature between Tg and Tx, and the heated BMG alloy can be pressed into a mold having the part shape to be molded. However, after injecting the BMG alloy into the mold, the part is not cooled to room temperature. BMG can be cooled to a temperature below Tg or slightly above Tg rather than at room temperature. The BMG gate can then be sheared using a cutting tool heated to a temperature between Tg and Tx, after which the BMG component can be further cooled to below Tg (eg, near room temperature). In short, in this embodiment, starting with an amorphous BMG alloy at a temperature below Tg, raising the temperature of this BMG alloy to above Tg, casting the BMG alloy with a mold part, and lowering the temperature of this molded part below Tg Or cut the part of this molded part using a hot cutting tool that has been heated to a temperature slightly above Tg and heated to above Tg (temperature in the supercooled liquid region of BMG alloys from Tg to Tx). it can. During cutting, the temperature of the entire molded part can be below Tg or above Tg, but the local temperature of the cutting zone surrounding the hot knife must be above Tg.

  In another embodiment, a molten BMG alloy is cast or molded into a BMG part shape at a temperature above Tg using a molten BMG alloy at a temperature above Tm, and then the BMG part is substantially throughout the BMG part. The BMG component is cooled to a temperature lower than Tg so that it becomes amorphous. Next, the BMG part region, where the BMG part is cut at a temperature above Tg, is locally heated or the entire BMG part is heated to a temperature above Tg to cut a portion of the BMG part. be able to.

  In one variation, a knife with a different texture or feature may be used so that when the BMG part is cut, the texture or feature is replicated on the BMG part. It is necessary to finish after cutting by cutting with a conventional water jet or saw. For example, it is necessary to finish a subsequent process such as polishing, shaving, or chamfering of a BMG part. By cutting a BMG part using a hot knife, these mechanisms can be incorporated into the knife and the BMG part can be cut using this hot knife without any subsequent finishing.

  Furthermore, embodiments of the present specification allow for clean cutting without causing local heating and crystallization in the region near the cutting surface, as would normally be expected with BMG parts using saw cutting. it can.

An exemplary method for forming and separating a bulk solidified amorphous alloy includes the following steps:
1) preparing a raw material for an amorphous alloy that is substantially amorphous;
2) heating the raw material, mold, and cutting tool to near the glass transition temperature or into the supercooled liquid region;
3) The process of putting the heated raw material into a mold, shaping it, separating the excess material, and shaping the desired shape;
4) cooling the temperature of the molded part to a temperature well below the glass transition temperature.

More specifically, the above-described exemplary method of forming and separating a bulk solidified amorphous alloy can be performed as follows with reference to FIGS. 3 (a) and 3 (b):
(1) Obtain a bulk amorphous alloy raw material and heat it to Tg-Tx.
(2) A heated bulk amorphous alloy is inserted (injected) into a mold to form a BMG component.
(3) The cutter having the temperature of Tg to Tx is operated to trim the BMG part. The BMG part may be less than Tg during cutting and the BMG part may be between Tg and Tx. BMG parts can be cooled during cutting.
(4) Open the mold and take out the trimmed BMG part. BMG parts may be cooled during removal.

Another exemplary method of forming and separating a bulk solidified amorphous alloy includes the following steps:
1. Preparing a homogeneous alloy raw material of an amorphous alloy (not necessarily amorphous);
2. Heating the raw material to a casting temperature above the melting temperature;
3. Introducing the molten alloy into a first mold having a critical casting thickness or less, and quenching the molten alloy to a temperature below the glass transition;
4). Heating the raw material, the second mold, and the cutting tool to near the glass transition temperature or in the supercooled liquid region;
5. The process of putting the heated raw material into a second mold, shaping it, separating the excess material, and molding the desired shape;
6). Cooling the temperature of the molded part to a temperature well below the glass transition temperature. This part may have a thickness greater than the critical casting thickness.
7). The second mold may not be necessary, i.e. all can be integrated into one mold.

More specifically, the above-described exemplary method of forming and separating a bulk solidified amorphous alloy can be performed as follows with reference to FIGS. 3 (a) and 3 (b):
(1) Obtain a metal alloy raw material (which may or may not be amorphous) and heat it to a temperature above Tm.
(2) The molten raw material is inserted (injected) into a mold shaped into a part shape.
(3) The molten raw material in the mold is cooled to less than Tg to form a BMG part.
(4) Trimming BMG parts by operating a cutter having a temperature of Tg to Tx. The BMG part may be less than Tg during cutting and the BMG part may be at a temperature between Tg and Tx. BMG parts can be cooled during cutting.
(5) Open the mold and take out the trimmed BMG part. BMG parts may be cooled during removal.

Microstructure Formation During Separation of Bulk Solidifying Amorphous Alloy Another embodiment relates to an apparatus for forming / casting BMG parts and cutting portions of BMG parts using a hot knife. The knife can be maintained at a heated temperature above Tg and have various types of microstructures to form a similar microstructure on the BMG part during cutting.

  The microstructure can include a hologram logo. This can be realized with a knife having a hologram negative, and as shown in FIGS. 4 (a) and 4 (b), when cutting a BMG part, the BMG part is cut in one step together with the BMG part cutting. A hologram can be formed on the part. In order not to damage the hologram, the knife may have a slight draft, so that when the knife is extracted, the microstructure formed on the BMG part is not damaged (it is already molded when the knife is extracted). May cause a small chamfer to be retained on top of the shape being

Claims (18)

A method for forming a part from a bulk solidified amorphous alloy comprising:
Before Symbol bulk-solidifying amorphous alloy of time - temperature profile, the bulk-solidifying amorphous alloy of time - temperature - that turning the crystallization region of the transformation (TTT) diagram, the steps of forming a component from the bulk-solidifying amorphous alloy ,
Cutting a portion of the part with a cutting tool heated to a temperature higher than the glass transition temperature (Tg) of the bulk solidified amorphous alloy. The forming step includes a step of heating the amorphous alloy to a region between Tg and a critical crystallization temperature (Tx) of the bulk solidified amorphous alloy, and a step of inserting the bulk solidified amorphous alloy into a mold. When the including method of claim 1.     The method of claim 1, wherein the cutting comprises shearing the portion of the part from the remaining portion of the part.     The method of claim 1, wherein during the cutting step, the temperature of the region of the part in contact with the cutting tool is greater than Tg and the rest of the part is less than Tg or greater than Tg. The step of molding the part comprises
Heating the bulk solidified amorphous alloy to a temperature equal to or higher than the melting temperature (Tm) of the bulk solidified amorphous alloy;
Inserting the bulk solidified amorphous alloy into a mold;
Cooling the bulk solidified amorphous alloy to a temperature below Tg.     The method of claim 5, wherein the cutting comprises shearing the portion of the part from the rest of the part.     The method of claim 6, wherein during the cutting step, the temperature of the region of the part in contact with the cutting tool is greater than Tg and the remaining part of the part is less than Tg or greater than Tg. A material containing a bulk-solidifying amorphous alloys, the glass transition temperature Tabimata of the bulk-solidifying amorphous alloy and heating to a temperature in the supercooled liquid region,
While the material is heated at the glass transition temperature or at a temperature within the supercooled liquid region ,
Forming a part from the material and separating excess material from the part. The bulk solidified amorphous alloy is represented by a molecular formula (Zr, Ti) _a (Ni, Cu, Fe) _b (Be, Al, Si, B) _c , where a is an atomic percentage, and a is 30 to 75. 9. The method of claim 8, wherein b is in the range of 5-60 and c is in the range of 0-50. The bulk solidified amorphous alloy is represented by the molecular formula (Zr, Ti) _a (Ni, Cu) _b (Be) _c , where a is an atomic percentage, a is in the range of 40 to 75, and b is 5 to 5 9. The method of claim 8, wherein c is in the range of 50 and c is in the range of 5-50.     9. The method of claim 8, wherein the material can withstand up to 1.5% or more strain without any permanent deformation or breakage. Preparing a raw material for a material including a bulk solidified amorphous alloy;
The raw material, the mold, and a cutting tool, the glass transition temperature Tabimata of the bulk-solidifying amorphous alloy and heating to a temperature in the supercooled liquid region,
Introducing the heated raw material into the mold to form a part having excess material;
Separating the excess material from the part with the cutting tool;
Cooling the temperature of the part to a temperature below the glass transition temperature of the bulk solidified amorphous alloy. A step of heating the alloy to a casting temperature equal to or higher than the melting temperature of the alloy, wherein the molten alloy is made by the step; and
Introducing the molten alloy into a mold;
Quenching the molten alloy to a temperature below the glass transition temperature of the alloy, wherein the process produces a part that at least partially includes an amorphous microstructure; and
And said component, a cutting tool, the glass transition temperature Tabimata of the alloy and heating to a temperature in the supercooled liquid region,
Separating excess material from the part;
Cooling the component to a temperature below the glass transition temperature.     The method of claim 8, wherein the separating comprises forming a microstructure on a surface of the part.     The method of claim 14, wherein the microstructure comprises a hologram. A time-temperature profile configured to form a part from a bulk solidified amorphous alloy and the time when forming the part does not enter the crystallization region in the time-temperature-transformation (TTT) diagram of the bulk solidified amorphous alloy A mold that is configured to be heated or cooled such that
A cutting tool, wherein the cutting tool is heated to a temperature above the glass transition temperature (Tg) of the bulk solidified amorphous alloy, and a portion of the part is removed while the temperature of the cutting tool is above Tg. A cutting tool configured to cut.     The apparatus of claim 16, wherein a surface of the cutting tool includes a microstructure, and the cutting tool is configured to form a microstructure on a surface of the part upon cutting the portion of the part. . Heating the alloy to a casting temperature equal to or higher than the melting temperature of the alloy to form a molten alloy;
Introducing the molten alloy into a mold;
Quenching the molten alloy to a temperature below the glass transition temperature (Tg) of the alloy to produce a part that at least partially includes an amorphous microstructure;
A cutting tool, and heating the glass transition temperature of the alloy, or a supercooled liquid region,
Separating excess material from the part with the heated cutting tool while the part is at a temperature below Tg.

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