Amorphous composites and methods of making the same

Abstract

The application relates to the material field and relates to an amorphous composite material and a preparation method thereof. a Cu b Al4Ag1Sn 0.75 , 43<=a<=55.25, 39<=b<=51.5; a+b=94.25; the amorphous composite material controls the thermodynamic precipitation enthalpy of the austenite phase B2-CuZr by regulating the molar ratio of alloy atoms Zr and Cu, simultaneously reduces the stacking fault energy of the martensitic phase transformation of the austenite phase B2-CuZr, and improves the martensitic phase transformation capacity of the austenite phase B2-CuZr. The austenite phase B2-CuZr in the amorphous composite material absorbs a large amount of strain energy by undergoing martensitic phase transformation in the deformation process, and the austenite and the martensite can hinder the expansion of shear bands in the amorphous matrix and promote the proliferation of shear bands, so that good plasticity and work hardening capacity are obtained, and the toughness and plasticity of the amorphous composite material are significantly improved.

Description

TECHNICAL FIELD

[0001] The present application relates to the field of materials, in particular, to an amorphous composite material and a preparation method thereof. BACKGROUND

[0002] Amorphous alloy is a new type of disordered metal material obtained by avoiding nucleation and crystallization through melt rapid cooling. Its structure is similar to that of liquid metal, with long-range disorder and short-range order atomic arrangement characteristics, and no dislocation, grain boundary and other crystal defects, thus having unique properties different from traditional crystal materials.

[0003] However, since amorphous alloy has no dislocation and grain boundary and other crystal structure defects, plastic deformation of the amorphous alloy is rapidly concentrated in a very narrow shear band after starting, causing material softening and disastrous brittle fracture, which seriously restricts its wider engineering application.

[0004] Some studies use in-situ generated dendrites to toughen amorphous alloy, which makes the tensile plasticity of the amorphous alloy show obvious improvement, but such a composite material still shows strain softening characteristics under tension. SUMMARY

[0005] The purpose of the embodiments of the present application is to provide an amorphous composite material and a preparation method thereof, and to improve the toughness and plasticity of the material.

[0006] It is found that deformation-induced martensitic transformation can effectively inhibit the room temperature brittleness and strain softening of amorphous alloy, i.e., transformation-induced plasticity. The principle of transformation-induced plasticity is that the martensitic transformation of austenite in the amorphous composite material occurs during deformation, absorbing a large amount of strain energy, and both austenite and martensite can hinder the expansion of shear bands in the amorphous matrix and promote the proliferation of shear bands, thereby obtaining good plasticity and work hardening capacity.

[0007] It is further found that, in order for the amorphous composite material to obtain the best room temperature tensile mechanical properties, firstly, a uniform distribution of single austenite phase of the amorphous composite material structure needs to be prepared; secondly, the austenite phase in the amorphous composite material structure needs to be easily transformed into martensite during deformation, thereby producing a significant transformation toughening effect.

[0008] Based on this, in a first aspect, the present application provides an amorphous composite material, the atomic mole ratio of the amorphous composite material is expressed as Zr a Cu b Al4Ag1Sn 0.75 , wherein 43≤a≤55.25, 39≤b≤51.5; a+b=94.25.

[0009] The amorphous composite provided in the application controls the thermodynamic precipitation enthalpy of the austenite phase B2-CuZr by regulating the molar ratio of alloy atoms Zr and Cu, and at the same time, reduces the stacking fault energy of the martensitic phase transformation of the austenite phase B2-CuZr, and improves the martensitic phase transformation capacity of the austenite phase CuZr. The austenite phase B2-CuZr in the amorphous composite absorbs a large amount of strain energy by undergoing martensitic phase transformation in the deformation process, and both the austenite and the martensite can hinder the expansion of the shear band in the amorphous matrix and promote the proliferation of the shear band, so as to achieve the significant improvement of the toughness and plasticity of the amorphous composite.

[0010] In other embodiments of the application, the molar ratio of Zr / Cu in the amorphous composite is 0.835-1.417.

[0011] Zr and Cu as main alloying elements directly affect the thermodynamic precipitation enthalpy of the austenite phase B2-CuZr in the amorphous composite. By regulating the molar ratio of the main elements Zr / Cu, the alloying element can not only regulate the size of the austenite phase B2-CuZr precipitation enthalpy, but also regulate the amorphous forming ability of the alloy, and regulate the martensitic phase transformation capacity of the austenite phase B2-CuZr. In the above technical solution, by controlling the molar ratio of Zr / Cu in the amorphous composite to be 0.835-1.417, the austenite phase B2-CuZr precipitation enthalpy can be controlled in a suitable range, so as to control the precipitation of the crystal phase in the amorphous composite, and the amorphous forming ability and the martensitic phase transformation capacity of the austenite phase B2-CuZr are in a good range.

[0012] Further optionally, the molar ratio of Zr / Cu in the amorphous composite is 0.9635-1.1061.

[0013] The ratio of Cu / Zr affects the thermodynamic precipitation enthalpy of the alloy toughening phase B2-CuZr, and further affects the grain size of the B2-CuZr phase in the solidification process of the amorphous composite. When Cu / Zr>1, the amorphous forming ability of the alloy is improved; when Cu / Zr<1, the stacking fault energy of the B2-CuZr phase is reduced, and the martensitic phase transformation capacity of the B2-CuZr phase is improved.

[0014] In the above technical solution, the amorphous forming ability and the martensitic phase transformation capacity of the amorphous composite are good.

[0015] Further optionally, the molar ratio of Zr / Cu in the amorphous composite is 1.1061.

[0016] In the above technical solution, the amorphous composite only forms a single B2-CuZr crystal phase, eliminates the impurity phase, and greatly improves the toughness and plasticity of the material.

[0017] In other embodiments of the present application, the crystal phase of the amorphous composite material is a single B2-CuZr phase.

[0018] In other embodiments of the present application, the average size of the B2-CuZr phase of the amorphous composite material is 10 μm to 20 μm.

[0019] In other embodiments of the present application, the amorphous composite material is capable of undergoing a martensitic phase transformation.

[0020] In other embodiments of the present application, the yield strength of the amorphous composite material is 1000 MPa to 1500 MPa.

[0021] In other embodiments of the present application, the elongation of the amorphous composite material is 8% to 12%.

[0022] In a second aspect, the present application provides a method for preparing an amorphous composite material, comprising:

[0023] The atom mole ratio of the amorphous composite material according to the first aspect is prepared and smelted into an alloy ingot;

[0024] The alloy ingot is suction casted.

[0025] In other embodiments of the present application, the smelting above comprises:

[0026] The arc smelting is adopted, and the current is maintained at 240 A to 280 A; the smelting is performed at least 4 times.

[0027] In other embodiments of the present application, the suction casting above comprises:

[0028] The alloy ingot is remelted under an inert atmosphere at less than atmospheric pressure, and then suction casted. BRIEF DESCRIPTION OF DRAWINGS

[0029] In order to more clearly illustrate the technical solutions of the embodiments of the present application, the drawings needed in the embodiments will be briefly introduced as follows, and it should be understood that the following drawings only show some embodiments of the present application, and therefore should not be regarded as a limitation on the scope, and for those skilled in the art, other related drawings can also be obtained without creative labor on the basis of these drawings.

[0030] Figure 1 The high temperature DSC curve of the amorphous composite material prepared for the embodiment at φ7 mm;

[0031] Figure 2 The X-ray diffraction pattern of the amorphous composite material prepared for the embodiment;

[0032] Figure 3 The Zr 47.5 Cu46.25 Al4Ag1Sn 0.75 Sample and Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 Backscattered electron topography of sample at φ7mm; Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 Sample has a heterogeneous white phase Zr5Sn3 (EDS result); dark color is B2-CuZr phase; light gray is amorphous phase;

[0033] Figure 4 Zr made for example (a) 47.5 Cu 46.25 Al4Ag1Sn 0.75 Sample and Zr (b) 49.5 Cu 44.75 Al4Ag1Sn 0.75 Sample is inlayed in the same resin after polishing and EBSD phase color map; Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 Sample B2-CuZr phase did not undergo martensitic transformation; Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 Sample underwent martensitic transformation after polishing;

[0034] Figure 5 Zr made for example 49.5 Cu 44.75 Al4Ag1Sn 0.75 Microstructure of amorphous composite, (b) is the enlarged microstructure of (a);

[0035] Figure 6 Zr made for example 49.5 Cu 44.75 Al4Ag1Sn 0.75 X-ray diffraction of amorphous composite;

[0036] Figure 7 Zr made for example 49.5 Cu 44.75 Al4Ag1Sn 0.75 Microstructure EBSD of amorphous composite after polishing, (a) is the phase color map of B2 ball after polishing at room temperature (25℃), B2-CuZr phase underwent martensitic transformation after polishing; (b) is the inverse pole figure color map of B2 ball after polishing;

[0037] Figure 8 Zr made for example 49.5 Cu44.75 Al4Ag1Sn 0.75 Tensile true stress-true strain curves of amorphous composite materials. Detailed Implementation

[0038] To make the objectives, technical solutions, and advantages of the embodiments of this application clearer, the technical solutions of the embodiments of this application will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of this application, and not all embodiments. The components of the embodiments of this application described and shown in the accompanying drawings can generally be arranged and designed in various different configurations.

[0039] Therefore, the following detailed description of the embodiments of this application provided in the accompanying drawings is not intended to limit the scope of the claimed application, but merely to illustrate selected embodiments of the application. All other embodiments obtained by those skilled in the art based on the embodiments of this application without inventive effort are within the scope of protection of this application.

[0040] It should be noted that similar labels and letters in the following figures indicate similar items. Therefore, once an item is defined in one figure, it does not need to be further defined and explained in subsequent figures.

[0041] In the description of the embodiments of this application, it should be understood that the indicated orientation or positional relationship is based on the orientation or positional relationship shown in the accompanying drawings, or the orientation or positional relationship that the product of this application is usually placed in when in use, or the orientation or positional relationship that is commonly understood by those skilled in the art. It is only for the convenience of describing this application and simplifying the description, and is not intended to indicate or imply that the device or component referred to must have a specific orientation, or be constructed and operated in a specific orientation. Therefore, it should not be construed as a limitation of this application.

[0042] In the description of the embodiments of this application, it should also be noted that, unless otherwise expressly specified and limited, the terms "set" and "connection" should be interpreted broadly. For example, they can refer to a fixed connection, a detachable connection, or an integral connection; they can refer to a direct connection or an indirect connection through an intermediate medium; and they can refer to the internal connection of two components. Those skilled in the art can understand the specific meaning of the above terms in this application based on the specific circumstances.

[0043] This application provides an amorphous composite material, wherein the atomic molar ratio of the amorphous composite material is expressed as Zr. a Cu b Al4Ag1Sn 0.75 , where 43≤a≤55.25, 39≤b≤51.5; a+b=94.25.

[0044] The amorphous composite provided in the present application controls the thermodynamic precipitation enthalpy of the austenite phase B2-CuZr by regulating the atomic mole ratio of alloy, and at the same time, reduces the stacking fault energy of the martensitic phase transformation of the austenite phase B2-CuZr, and improves the martensitic phase transformation ability of the austenite phase B2-CuZr. The austenite phase B2-CuZr in the amorphous composite absorbs a large amount of strain energy by undergoing martensitic phase transformation during deformation, and both the austenite and the martensite can hinder the expansion of shear bands in the amorphous matrix and promote the proliferation of shear bands, so as to obtain good plasticity and work hardening capacity, thereby realizing the significant improvement of the toughness and plasticity of the amorphous composite.

[0045] Further optionally, in some embodiments of the present application, the atomic mole ratio expression of the amorphous composite described above is Zr a Cu b Al4Ag1Sn 0.75 , wherein 43≤a≤55.25, 39≤b≤51.5; a+b=94.25. Further optionally, the atomic mole ratio expression of the amorphous composite described above is Zr a Cu b Al4Ag1Sn 0.75 , wherein 44≤a≤55, 40≤b≤51; a+b=94.25. Exemplarily, a is 43, 44, 45, 46, 47, 48, 49, 50, 51, 52, 53, 54, 55, or a range between any two of the above values; b is 39, 40, 41, 42, 43, 44, 45, 46, 47, 48, 49, 50, 51, or a range between any two of the above values.

[0046] Further, in some embodiments of the present application, the amorphous composite described above is Zr x Cu (94.25-x) Al4Ag1Sn 0.75 (X=43, 46.25, 49.5, 55.25). Exemplarily, the amorphous composite described above is Zr 43 Cu 51.5 Al4Ag1Sn 0.75 , Zr 46.25 Cu 48 Al4Ag1Sn 0.75 , Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 , Zr 55.25 Cu 39 Al4Ag1Sn 0.75 .

[0047] Further, in some embodiments of the present application, the molar ratio of Zr / Cu in the amorphous composite material is 0.835-1.417.

[0048] Zr and Cu as main alloying elements directly affect the thermodynamic precipitation enthalpy of the austenite phase CuZr in the amorphous composite material. By regulating the molar ratio of the main elements Zr / Cu, the size of the austenite phase CuZr precipitation enthalpy of the alloy can be regulated, and the amorphous forming ability of the alloy can also be regulated, and the martensitic transformation ability of the austenite phase CuZr can also be regulated. In the above technical solution, by controlling the molar ratio of Zr / Cu in the amorphous composite material to be 0.835-1.417, the austenite phase CuZr precipitation enthalpy can be controlled within a suitable range, so as to control the precipitation of the crystal phase in the amorphous composite material, and the amorphous forming ability and the martensitic transformation ability of the austenite phase CuZr are within a good range.

[0049] Further optionally, the molar ratio of Zr / Cu in the amorphous composite material is 0.9635-1.1061.

[0050] Exemplarily, in some embodiments of the present application, the molar ratio of Zr / Cu in the amorphous composite material is: 0.835, 0.90, 0.95, 0.9635, 0.97, 0.98, 1.1061, 1.11, 1.12, 1.13, 1.14, 1.417 or a range between any two of the above values.

[0051] The molar ratio of Zr / Cu directly affects the precipitation of the austenite phase B2-CuZr phase; the austenite phase B2-CuZr phase as a toughening phase of the amorphous composite material can greatly improve the toughness and plasticity of the material.

[0052] The driving force of alloy phase transition thermodynamics and kinetics jointly controls the nucleation and growth of the crystal phase. Thermodynamically, the eutectoid reaction (Cu 10 The greater the enthalpy value of the B2-CuZr phase precipitation, the greater the thermodynamic driving force of the B2-CuZr phase precipitation. By regulating the alloy composition to regulate the B2-CuZr phase precipitation enthalpy of the alloy, the growth driving force of the B2-CuZr phase is reduced, and the B2-CuZr phase size is refined. Kinetically, according to the classical nucleation theory, the inverse of the nucleation rate I is the solidification time t, and the shorter the solidification time, the higher the nucleation rate. By preparing round rods of different diameters, the greater the diameter, the slower the cooling rate. The condition for the alloy to achieve uniform nucleation is that a large number of nucleation occurs in a very short time, which is beneficial to refining the B2-CuZr phase size of the amorphous composite material.

[0053] In the present application, the ratio of Cu / Zr affects the thermodynamic precipitation enthalpy of the alloy toughening phase B2-CuZr phase, and further affects the grain size of the B2-CuZr phase in the amorphous composite during the solidification process. When Cu / Zr>1, the amorphous forming ability of the alloy is improved; when Cu / Zr<1, the stacking fault energy of the B2-CuZr phase is reduced, and the martensitic transformation ability of the B2-CuZr phase is improved.

[0054] In the above technical solution, the amorphous composite has good amorphous forming ability and martensitic transformation ability.

[0055] Further, the molar ratio of Zr / Cu in the amorphous composite is 1.1061.

[0056] In the above technical solution, the amorphous composite only forms a single B2-CuZr phase crystal phase, eliminating impurities and greatly improving the toughness and plasticity of the material.

[0057] Further, in some embodiments of the present application, the crystal phase of the amorphous composite is a single B2-CuZr phase.

[0058] In some embodiments of the present application, an X-ray diffractometer (XRD) can be used to detect the crystal phase of the amorphous composite.

[0059] In some embodiments of the present application, when the Zr atomic ratio content increases to 55.25, the alloy precipitates an impurity phase CuZr2; when the Zr atomic ratio content decreases to 46.25, the alloy precipitates an impurity phase Cu 10 Zr7; when the Zr atomic ratio content decreases to 43, the amorphous forming ability of the alloy is improved. It is shown that too much or too little Zr content will precipitate impurities. When the Zr atomic ratio content is 47.5-49.5, the amorphous composite is composed of B2-CuZr phase and amorphous phase under X-ray diffraction.

[0060] Further, in some embodiments of the present application, the crystal phase of the amorphous composite with Zr atomic ratio content of 47.5-49.5 can be further detected by field emission scanning electron microscope backscattering mode. When the Zr atomic ratio content is 47.5, the amorphous composite contains an impurity phase Zr5Sn3 (white phase); when the Zr atomic ratio content is 49.5, the amorphous composite only contains a single B2-CuZr phase.

[0061] In some embodiments of the present application, when the Zr atomic ratio content is greater than 47.5 and less than or equal to 49.5, the amorphous composite only contains a single B2-CuZr phase, and the amorphous composite has very excellent toughness and plasticity.

[0062] Further, in some embodiments of the present application, the average size of the B2-CuZr phase of the amorphous composite material is 10 μm to 20 μm.

[0063] Further alternatively, in some embodiments of the present application, the average size of the B2-CuZr phase of the amorphous composite material is 11 μm to 19 μm.

[0064] Illustratively, in some embodiments of the present application, the average size of the B2-CuZr phase of the amorphous composite material described above is 12 μm, 13 μm, 14 μm, 15 μm, 16 μm, 17 μm, 18 μm, or a range between any two of the above-mentioned values.

[0065] Further, in some embodiments of the present application, the amorphous composite material is capable of undergoing a martensitic phase transition at room temperature.

[0066] Illustratively, in some embodiments of the present application, the B2-CuZr phase of the amorphous composite material is capable of undergoing a martensitic phase transition at 20 °C, 21 °C, 22 °C, 23 °C, 24 °C, 25 °C, 26 °C, 27 °C, 28 °C, 29 °C, 30 °C, or a range between any two of the above-mentioned values.

[0067] The ability of the B2-CuZr phase to undergo a martensitic phase transition during deformation has an important influence on the mechanical properties. The B2-CuZr phase is very stable at room temperature and is difficult to initiate a martensitic transition; the TRIP effect is weakened, and the mechanical properties are poor. By means of alloying to control the stability of the B2-CuZr phase, ensuring the occurrence of a martensitic transition behavior during deformation, and ensuring the sufficiency of the TRIP effect, the macroscopic mechanical properties of the composite material can be optimized.

[0068] Further, in some embodiments of the present application, the yield strength of the amorphous composite material is 1000 MPa to 1500 MPa.

[0069] Further alternatively, in some embodiments of the present application, the yield strength of the amorphous composite material is 1001 MPa to 1549 MPa.

[0070] Illustratively, in some embodiments of the present application, the yield strength of the amorphous composite material is 1005 MPa, 1105 MPa, 1200 MPa, 1300 MPa, 1400 MPa, 1500 MPa, or a range between any two of the above-mentioned values.

[0071] Further, in some embodiments of the present application, the elongation of the amorphous composite material is 8% to 12%. Further alternatively, the elongation of the amorphous composite material is 9.5% to 12%.

[0072] Further optionally, in some embodiments of the present application, the elongation of the amorphous composite material is 9% to 11%.

[0073] Illustratively, in some embodiments of the present application, the elongation of the amorphous composite material is 8%, 9%, 10%, 11%, or a range between any two of the aforementioned values.

[0074] The alloying components and preparation process of the present application refine the size and distribution of the B2-CuZr phase in the amorphous composite material, eliminate impurity phases, and at the same time improve the phase transition ability of the B2-CuZr phase. The composite structure generates a large number of high-density shear band networks through a large number of fine and dispersed B2-CuZr phases, thereby producing strong work hardening ability and excellent elongation.

[0075] Some embodiments of the present application provide a method for preparing an amorphous composite material, comprising:

[0076] The amorphous composite material provided according to any one of the preceding embodiments is prepared according to the atomic molar ratio of the components, and is melted into an alloy ingot.

[0077] The alloy ingot is suction cast.

[0078] Further, in some embodiments of the present application, the method for preparing an amorphous composite material comprises the following steps:

[0079] Step S1, melting.

[0080] In some embodiments of the present application, the amorphous composite material provided according to any one of the preceding embodiments is prepared according to the atomic molar ratio of the components, and is melted into an alloy ingot.

[0081] Further, in some embodiments of the present application, the melting comprises:

[0082] Arc melting is used, and the current is maintained at 240A to 280A; the melting is performed at least 4 times.

[0083] Further optionally, in some embodiments of the present application, the melting comprises:

[0084] Arc melting is used, and the current is maintained at 241A to 279A; the melting is performed at least 4 times.

[0085] Illustratively, in some embodiments of the present application, the melting comprises:

[0086] Arc melting is used, and the current is maintained at 241A, 245A, 250A, 255A, 260A, 265A, 270A, 279A, or a range between any two of the aforementioned values.

[0087] Further, in some embodiments of the present application, the melting is repeated for 4 to 6 times; for example, the melting is repeated for 4, 5 or 6 times.

[0088] By melting at least 4 times, an alloy ingot with uniform composition can be obtained.

[0089] Further, in some embodiments of the present application, the melting is performed in an inert gas atmosphere.

[0090] For example, in some embodiments of the present application, the pure elements are arc melted in a vacuum arc melting furnace with a high purity argon atmosphere for oxygen absorption of titanium, and the current is maintained at 240-280 A. The melting is repeated at least 4 times to ensure that an alloy ingot with uniform composition is obtained.

[0091] Step S2, suction casting.

[0092] The alloy ingot is subjected to suction casting.

[0093] Further, in some embodiments of the present application, the suction casting comprises:

[0094] The alloy ingot is remelted in an inert atmosphere at less than atmospheric pressure, and then subjected to suction casting.

[0095] Further, in some embodiments of the present application, the inert atmosphere is argon.

[0096] For example, in some embodiments of the present application, the alloy superheated melt is sucked into the cavity of a water-cooled conical copper mold by using the suction casting device of the melting furnace, to obtain a conical rod with different diameters. The diameter of the rod can be selected according to actual needs, for example, the diameter of the rod is selected to be 1 mm to 9 mm. For example, the diameter of the rod is 2 mm, 3 mm, 4 mm, 5 mm, 6 mm, 7 mm, 8 mm, 9 mm; or a range between any two of the above values.

[0097] The Zr-based amorphous alloy prepared in the present application has strong glass forming ability, and can be prepared into a large-size bulk amorphous alloy by using a less complex device. The Zr-based amorphous composite material not only has excellent performance of amorphous alloy, but also the second phase B2-CuZr phase in the composite material can effectively complement the performance of the matrix material, improve the comprehensive performance of the amorphous composite material, and expand the application prospect of the amorphous material. In addition to having been applied in some products such as golf club heads and solar wind collectors for space travel, the zirconium-based amorphous alloy is also a potential armor-piercing material.

[0098] Some specific embodiments are listed below to better illustrate the present application.

[0099]

Preparation of amorphous composite material

[0100] Provided is an amorphous composite material, prepared according to the following steps:

[0101] (1) Ingredients:

[0102] According to Zr x Cu (94.25-x) Al4Ag1Sn 0.75 (X=43, 46.25, 47.5, 49.5, 55.25) alloy composition, select pure elements and weigh the ingredients in proportion.

[0103] (2) Arc melting and suction casting: In a vacuum arc melting furnace with high-purity argon atmosphere for titanium oxygen absorption, the ingredients of each pure element are arc melted, and the current is maintained at 260 A. The alloy ingot is melted for 5 times to ensure uniform composition. Then, the over-heated alloy melt is sucked into the cavity of a water-cooled copper mold using the suction casting device of the melting furnace to obtain a rod with a diameter of 7 mm.

[0104] The parameters of each embodiment are shown in Table 1.

[0105] Table 1

[0106] Atomic molar ratio expression Zr / Cu Example 1 Zr 43 Cu 51.5 Al4Ag1Sn 0.75 ]]> 0.8350 Example 2 Zr 46.25 Cu 48 Al4Ag1Sn 0.75 ]]> 0.9635 Example 3 Zr 47.5 Cu 46.75 Al4Ag1Sn 0.75 ]]> 1.0160 Example 4 Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 ]]> 1.1061 Example 5 Zr 55.25 Cu 39 Al4Ag1Sn 0.75 ]]> 1.4167

[0107] The properties of the amorphous composite materials obtained in each embodiment are detected.

[0108] 1. Detection of B2-CuZr phase precipitation enthalpy.

[0109] The tip sample of the above alloy conical rod is tested using a high-temperature differential scanning calorimeter (DSC) with a heating rate of 20℃ / min, and the DSC curve is obtained, as shown in Figure 1 The B2-CuZr phase precipitation enthalpy of the amorphous composite material of each embodiment is calculated and analyzed according to the DSC curve. As can be seen from Figure 1 , with the increase of Zr content, the B2-CuZr phase precipitation enthalpy first increases and then decreases, which shows that the B2-CuZr phase precipitation enthalpy is controlled by adjusting the Cu / Zr ratio of the alloy.

[0110] 2. Phase analysis.

[0111] The phase of the sample at the 7mm diameter of the amorphous composite material rod provided in each embodiment is analyzed using an X-ray diffractometer (XRD), as shown in Figure 2 . As can be seen from Figure 2 , when the Zr atomic ratio content increases to 55.25, the alloy precipitates a heterogeneous phase CuZr2; when the Zr atomic ratio content decreases to 46.25, the alloy precipitates a heterogeneous phase Cu 10 Zr7; when the Zr atomic ratio content decreases to 43, the amorphous forming ability of the alloy is improved. It shows that too much or too little Zr content will precipitate heterogeneous phases.

[0112] From Figure 2 It can be seen that the alloy composition Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 and Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 is an amorphous composite material composed of B2-CuZr phase and amorphous phase under X-ray diffraction.

[0113] 3, topography detection.

[0114] The Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 sample and the Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 sample were observed by field emission scanning electron microscopy backscattering mode, and see Figure 3 . It can be seen from Figure 3 that the Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 sample contains impurity phase Zr5Sn3 (white phase); the Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 sample only contains single B2-CuZr phase.

[0115] 4, martensitic transformation ability detection.

[0116] EBSD technology was used to analyze the phase structure of the Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 sample and the Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 sample after polishing at room temperature (25℃), see Figure 4 . It can be seen from Figure 4 that the B2-CuZr phase of the Zr 47.5 Cu 46.25 Al4Ag1Sn 0.75 sample is still B2-CuZr phase after polishing; and the B2-CuZr phase in the Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 sample has undergone martensitic transformation after polishing; it is proved that the application controls the martensitic transformation ability of the B2-CuZr phase in the alloy by controlling the Cu / Zr ratio.

[0117] Further to the Zr49.5 Cu 44.75 Al4Ag1Sn 0.75 The B2-CuZr phase morphology and distribution of the samples were observed by field emission scanning electron microscopy, see Figure 5 ; the phase of the samples was analyzed by X-ray diffractometer, see Figure 6 ; the microstructure of the polished sample was analyzed by EBSD technology, see Figure 7 .

[0118] It can be seen from Figure 5 that Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The sample only contains a single B2-CuZr phase.

[0119] It can be seen from Figure 6 that Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The sample only contains a single B2-CuZr phase.

[0120] It can be seen from Figure 7 that Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The sample only friction occurs martensitic transformation.

[0121] 5, elongation detection.

[0122] The Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The sample was cut into a dog bone-shaped sample with a gauge section of 6mm x 1.5mm x 1.5mm for tensile testing:

[0123] The test method is: mechanical test on Instron million mechanical testing machine, tensile sample is cut from round bar, dog bone shape, sample gauge section cross section 1.5 x 1.5mm, gauge section length 6.5mm, using 5mm extensometer to measure strain, loading rate is 2.5 x 10 -4 / s.

[0124] The mechanical properties of the sample are shown in Figure 8 . The true stress true strain curve is corrected as follows: true stress σ = σ 名义值 x (1 + ε 名义值 ); true strain ε = ln (1 + ε 名义值 ).

[0125] According to Figure 8 , it can be concluded that the above Zr 49.5 Cu 44.75Al4Ag1Sn 0.75 The yield strength of the sample is 1220Mpa, and the elongation is 9.5%.

[0126] The performance test results of each embodiment are shown in Table 2.

[0127] Table 2

[0128]

[0129] In summary, the scheme of the present application can regulate the B2-CuZr phase precipitation enthalpy in the alloy, the amorphous forming ability of the alloy, and the martensitic transformation ability of the B2-CuZr phase by regulating the Zr / Cu molar ratio of the amorphous composite. Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The sample is prone to martensitic transformation (only friction can occur), and the B2-CuZr phase grain size is very small (average size 15μm), and has very excellent elongation and work hardening capacity, the yield strength is 1220Mpa, and the elongation is 9.5%.

[0130] The embodiments described above are part of the embodiments of the present application, rather than all the embodiments. The detailed description of the embodiments of the present application is not intended to limit the scope of the claimed application, but only represents selected embodiments of the present application. Based on the embodiments in the present application, all other embodiments obtained by those of ordinary skill in the art without creative labor are within the scope of protection of the present application.

Claims

1. An amorphous composite material, characterized in that, The atomic molar ratio expression for the amorphous composite material is Zr 49.5 Cu 44.75 Al4Ag1Sn 0.75 The crystalline phase of the amorphous composite material is a single B2-CuZr phase. After polishing, the B2-CuZr phase in the amorphous composite material undergoes a martensitic phase transformation. The average size of the B2-CuZr phase in the amorphous composite material is 10μm~20μm.

2. The amorphous composite material according to claim 1, characterized in that, The molar ratio of Zr / Cu in the amorphous composite material is 1.1061.

3. The amorphous composite material according to claim 1 or 2, characterized in that, The yield strength of the amorphous composite material is 1000 MPa to 1500 MPa.

4. The amorphous composite material according to claim 1 or 2, characterized in that, The elongation of the amorphous composite material is 8%~12%.

5. The method for preparing the amorphous composite material according to any one of claims 1-4, characterized in that, include: The amorphous composite material is prepared according to the atomic molar ratio of claim 1 and melted into an alloy ingot; The alloy ingot is vacuum cast.

6. The method for preparing the amorphous composite material according to claim 5, characterized in that, The smelting includes: Electric arc melting is used, with the current maintained at 240 A to 280 A; melting is performed at least 4 times.

7. The method for preparing the amorphous composite material according to claim 5, characterized in that, include: The suction casting includes: The alloy ingot is remelted in an inert atmosphere at less than atmospheric pressure and then vacuum-cast.

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