AMORPHOUS ALLOY DIE CAST AND HEAT TREATMENT PROCESS OF THE SAME

Abstract

A heat treatment process for an amorphous alloy die cast comprises: the amorphous alloy die cast is subjected to an aging treatment at a temperature of about 0.5-0.6 Tg, for a time of about 10 minutes to about 24 hours. The amorphous alloy die cast comprises Zr, and is represented by a formula of (Zr1−xTix)a(Cu1−yNiy)bAlcMd, in which M is selected from the group consisting of: Be, Y, Sc, La, and combinations thereof, 38≦a≦65, 0≦x≦0.45, 0≦y≦0.75, 20≦b≦40, 0≦c≦15, 0≦d≦30, and the sum of a, b, c, and d in atomic percentages equals to 100.

Description

CROSS-REFERENCE TO RELATED APPLICATION

The present application is a continuation of International Patent Application No. PCT/CN2011/077762, filed Jul. 28, 2011, entitled “AMORPHOUS ALLOY DIE CAST AND HEATING PROCESS OF THE SAME”, which claims the priority and benefit of Chinese Patent Application No. 201010244468.7, filed with the State Intellectual Property Office of the P. R. China on Jul. 29, 2010. The entire content of both applications are incorporated herein by reference.

FIELD OF THE PRESENT DISCLOSURE

The present disclosure relates to methods of manufacturing amorphous alloys, more particularly to an amorphous alloy die cast and a heat treatment process of the same.

BACKGROUND

Extensive research and numerous experiments demonstrated that crystal boundaries, dislocations, stacking faults, or other crystal defects do not exist in amorphous alloys. Hence, amorphous alloys possess a plurality of advantageous material properties that crystal metals do not have, such as better corrosion resistance, higher frictional resistance, and improved magnetic and electric properties. Amorphous alloys are widely used in electronic, mechanical, chemical, and national defense industries.

At present, bulk amorphous alloy, also known as metallic glass, is usually formed by rapid cooling of melted metal alloy to a temperature below the glass transition temperature. It is believed that rapid cooling may prevent the formation and growth of crystal nucleus. Thus the melted alloy may solidify directly to form amorphous alloy which has a long range disordered structure. Bulk amorphous alloys usually are millimeter-sized. Nowadays, bulk amorphous alloys are mainly prepared in research laboratories. Amorphous alloys may be prepared by several processes including melting and suction-casting process in an electrical arc furnace, solvent packaging process, water quenching process, or other processes. However, in these processes, preparation of bulk amorphous alloys to achieve desired material properties may require stringent processing conditions, such as highly purified raw materials, high degree of vacuum, very rapid cooling, etc. These processes may not be applicable in the manufacturing industry because of their high costs and low efficiencies.

Therefore, large corporations and research institutes are both seeking for an amorphous alloy preparation process suitable for high volume manufacturing under normal processing conditions. Die casting is one of the most popular methods for preparing amorphous alloys. However, material properties are usually unstable for amorphous alloys prepared by present die castings processing method under current available conditions. Thus, the applications of amorphous alloys obtained by die casting are very limited.

Chinese Patent Application Publication No. CN101550521A discloses a rare-earth-based bulk amorphous alloy and its composite material. The composite material is obtained based on the bulk amorphous alloy through a heat treatment process. The heat treatment process includes an isothermal annealing of the rare-earth-based bulk amorphous alloy in a furnace at a temperature within the supercooled liquid region (325-650° C.). The process is performed in a 10⁻³ Pa vacuum environment. The composite material prepared thereof has improved thermal stability, higher electrical resistance, good soft magnetic property, and excellent processing capability in the supercooled liquid region. However, this heat treatment process requires relatively high annealing temperature. The temperature required must reside in the supercooled liquid region and is higher than the glass transition temperature Tg. Hence, the annealing process may cause portion of the amorphous alloy become crystallized.

SUMMARY

The present disclosure aims to solve at least one of the foregoing problems, including the unstable properties of amorphous alloy obtained by die-casting techniques and complexity associated with known processes of bulk amorphous alloy preparation.

One embodiment of the present disclosure provides a novel heat treatment process of an amorphous alloy die cast. The heat treatment process includes an aging treatment performed to the amorphous alloy die cast at a temperature of about 0.5 Tg to about 0.6 Tg for a time period of about 10 minutes to about 24 hours.

In one embodiment, the amorphous alloy die cast may be prepared by a low-speed die casting process in a vacuum environment. The process is performed under a pressure of about 50 Pascal (Pa) to about 200 Pa, with a die casting speed of about 3 meter per second (m/s) to about 5 m/s. The amorphous alloy die cast may have a thickness of about 0.5 millimeter (mm) to about 2 mm.

In some embodiments, the aging process may be performed in a positive pressure of about 0.1 MPa to about 0.5 MPa.

In some embodiments, the amorphous alloy die cast may have a thickness of about 1.0 mm to about 1.5 mm. The aging treatment may be performed at a temperature of about 0.53 Tg to about 0.57 Tg, for a time period of about 30 minutes to about 60 minutes.

In another embodiment of the present disclosure, a Zirconium (element Zr) based amorphous alloy die cast is provided. The Zirconium based amorphous alloy die cast may be prepared by the heat treatment processes described above. The Zirconium based amorphous alloy die cast may be composed of (Zr_1−xTi_x)_a(Cu_1−yNi_y)_bAl_cM_d, wherein M may be selected from the group consisting of Be, Y, Sc, La, and combinations thereof; and 38≦a≦65, 0≦x≦0.45, 0≦y≦0.75, 20≦b≦40, 0≦c≦15, 0≦d≦30; and the sum of a, b, c, and d in atomic percentages equals to 100.

In various embodiments, the amorphous alloy die cast obtained by the disclosed heat treatment process exhibits higher bending resistance and decreased property instability.

While the amorphous alloys and methods thereof will be described in connection with various preferred illustrative embodiments, it will be understood that it is not intended to limit the amorphous alloy die casts and methods thereof to those embodiments. On the contrary, it is intended to cover all alternatives, modifications, and equivalents as may be included within the spirit and scope of the disclosed subject matter as defined by the appended claims.

BRIEF DESCRIPTION OF THE DRAWINGS

These and other aspects and advantages of the present disclosure will become apparent and more readily appreciated from the following descriptions taken in conjunction with the drawings, in which:

FIG. 1 shows the X-ray Diffraction (XRD) patterns of samples A1, B1, and C1 according to an embodiment of the present disclosure; and

FIG. 2 shows the Differential Scanning calorimetry (DSC) patterns of samples A1, B1, and C1 according to an embodiment of the present disclosure.

DETAILED DESCRIPTION OF THE EMBODIMENTS

Traditional amorphous alloy die cast is usually not subjected to heat treatment. During the high-pressure, high-speed casting process of traditional metal alloys such as Aluminum alloys, Zinc alloys, or Magnesium alloys, gas in the die cast mold can be unavoidably trapped inside the die cast and form subsurface porosities. If the die cast is subsequently subjected to a heat treatment process, gas bubbles may be formed at the surface, causing deformation of the die cast. Hence, both the properties and the appearance of the die cast are negatively affected.

In contrast to traditional Aluminum, Zinc, Magnesium or their combinational alloys, amorphous alloy has a low temperature supercooled liquid region. The disclosed subject matter provides a novel process method that utilizes this supercooled liquid region to significantly reduce the gas trapped in the amorphous alloy comparing to that in the traditional metal alloys. Specifically, the disclosed subject matter provides a die casting process that is performed under a vacuum pressure of about 50 Pa to about 200 Pa, and at a low die casting speed of about 3 m/s to about 5 m/s. In addition, risk of die cast bubbling during heat treatment may be effectively eliminated if the post die cast heat treatment is performed under atmospheric pressure or positive pressure, i.e., about 0.1 Pa to about 0.5 MPa, in the range of middle to high pressure.

One embodiment of the present disclosure discloses a novel heat treatment process of an amorphous alloy die cast. The heat treatment process comprises two steps.

The first step comprises die casting and molding the amorphous alloy die cast at a pressure of about 50 Pa to about 200 Pa and at a die casting speed of about 3 m/s to about 5 m/s. The resulted amorphous alloy die cast may have a thickness ranging from about 0.5 mm to about 2 mm, with most of the die casts having thicknesses ranging from about 1.0 mm to about 1.5 mm.

The second step comprises performing an aging treatment on the amorphous alloy die cast, at a temperature of about 0.5 Tg to about 0.6 Tg, for a time period of about 10 minutes to about 24 hours. Tg refers to the glass transition temperature measured in Kelvin. A particular Tg of a certain amorphous alloy may be obtained by DSC testing. DSC testing is a currently known technique. The aging treatment may be performed at atmospheric pressure or positive pressure. In some embodiments, a positive pressure of about 0.1 MPa to about 0.5 MPa is preferred in order to prohibit gas from diffusing to the surface of the die cast. In some embodiments, the preferred aging temperature is about 0.53 Tg to about 0.57 Tg and the preferred aging time period is about 30 minutes to about 60 minutes for a amorphous alloy die cast with a thickness of about 1.0 mm to about 1.5 mm. Corresponding to different thicknesses of the die cast, the preferred aging treatment temperature may be increased or decreased; and the preferred heat treatment time period may be shortened or extended. However, the aging treatment should be kept within about 0.5 Tg to about 0.6 Tg range.

In various embodiments of the present disclosure, the amorphous alloy die cast that is subjected to the above disclosed heat treatment process neither crystallizes, nor has gas bubbles at the surface. The die cast exhibits improved material properties and enhanced stability. These improvements may be attributed to the following reasons.

First, during the amorphous alloy die cast preparation process, the die cast is cooled off after molding. Cooling rates at different parts of the die cast are different. The different cooling rates may cause some weak areas or stress concentration regions. In the present disclosure, the low aging treatment temperature ranging from about 0.5 Tg to about 0.6 Tg enables the relaxation and releasing of the concentrated stresses. Hence, the process disclosed in the present disclosure prevents the amorphous alloy die cast from premature fracturing before the material's yield point is reached. As a result, the material's performance and stability of the die cast are improved.

Second, the amorphous alloy die cast is formed at a vacuum pressure of about 50 Pa to about 200 Pa and at a low casting speed of about 3 m/s to about 5 m/s. Because the amorphous alloy has a high viscosity, the amount of gases trapped within the amorphous alloy die cast is less than that in the traditional alloy die casts. During subsequent aging treatment performed under middle to high pressure (about 0.1 MPa to about 0.5 MPa), the positive pressure prohibits the trapped gas from diffusing to the surface of the amorphous alloy die cast.

Third, when amorphous alloy is rapidly cooled, the microstructure of the amorphous alloy is in a highly disordered and unstable state. While the low temperature aging treatment may not provide sufficient energy to overcome the energy barrier required for crystallization, it can overcome the metastable energy barrier and enable the transformation of the material structure from a high-energy long-range disordered state to a short-range ordered state. Here, the low temperature aging refers to aging treatment performed below the glass transition temperature. The current disclosure discloses that such a temperature range is from about 0.5 Tg to about 0.6 Tg.

After the low temperature aging process, the alloy may become, for example, pentagonal or dodecagonal quasicrystals, both have short-range ordered structures. Although the short-range ordered structure cannot grow to become crystal, (the crystallization process requires re-melting into a disordered state), it can enhance the stability of the material properties. Referring to FIG. 2, after the aging treatment, the die cast exhibits an increased area under the crystallization peak. The increased area under the crystallization peak indicates more energy is released during the crystallization and in turn, indicates a more stable crystal structure and a more stable material property.

Reference will be made in detail to embodiments of the present disclosure. The embodiments described herein with reference to drawings are explanatory, illustrative, and used to generally understand the present disclosure. The embodiments shall not be construed to limit the present disclosure. The same or similar elements and the elements having same or similar functions are denoted by like reference numerals throughout the descriptions.

In the two embodiments disclosed, aging treatments were performed on two typical Zr-based amorphous alloys composed of Zr₅₅Al₁₅Cu₂₅Ni₅ and Zr₄₁Ti₁₄Cu₁₅Ni₁₀Be₂₀, respectively. The two amorphous alloys have excellent glass forming ability, excellent mechanical properties and broad supercooled liquid region. Therefore, these two typical Zr-based alloys are selected to explain the effects of the aging treatment on the amorphous alloys.

In the first embodiment, high purity (purity is greater than 99.0 wt %) Zr, Al, Cu, and Ni with a weight ratio corresponding to the composition of Zr₅₅Al₁₅Cu₂₅Ni₅ were melted in an electrical arc furnace. Subsequently, a copper mould was used for die casting in the presence of a protective Argon gas. The die casting was performed in a condition of a pressure of 150 Pa and a casting speed of 3m/s. Fifteen amorphous alloy die casts were prepared for experimental purposes, each having a size of 80 mm×6 mm×1.5 mm. The fifteen amorphous alloy die casts were labeled as A1 to A15, and having a composition of Zr₅₅Al₁₅Cu₂₅Ni₅. The glass transition temperature Tg was determined to be 704K for this type of alloy by performing a DSC test. The fifteen die casts were divided into three groups.

The first group includes A1 to A5, all of which were not subjected to any aging treatments.

The second group includes A6 to A10, each of which was subjected to an aging treatment in a pressure of 0.2 MPa, at a temperature of 0.53 Tg (373K) , for a time period of 1 hour. The resulted die casts were labeled as B1 to B5.

The third group includes A11 to A15, each of which was subjected to an aging treatment in a pressure of 0.2 MPa, at a temperature of 0.81 Tg (573K) , for a time period of 1 hour. The resulted die casts were labeled as C1 to C5.

Property Tests

1) Bending Resistance Test

Pursuing to standard bending resistance test disclosed in GB/T14452-93 and using a CMT5105 universal material testing machine, the three-point bending fracturing tests were performed on each of the die casts groups A1-A5, B1-B5, and C1-C5. The resulted strength values were recorded. The average and variance of the strength values were calculated. All data are shown in Table 1.

2) XRD (X-Ray Diffraction) Analysis

In order to determine whether the alloy is amorphous, X-ray powder diffraction analyses were performed on die cast samples A1, B1, and C1. A D-MAX2200PC X-ray powder diffraction instrument was used, and the XRD analyses were performed under the following conditions: X-ray radiation was generated by a copper target; the incident wavelength X is 1.54060A; the accelerating voltage is 40 KV; the current is 20 mA; and the scan step is 0.04° . The XRD results are shown in FIG. 1. It can be seen that A1 and B1 have amorphous structures and C1 has a crystal structure (the sharp diffraction peaks of C1 indicate a crystal structure).

3) DSC Test

DSC tests were performed on A1, B1, and C1 with a STA409 Thermogravimetric and Differential Thermal Analyzer. An 99% pure Al₂O₃ crucible was selected. The results are shown in FIG. 2. It can be seen that Bl, which was subjected to an aging treatment at a temperature of 0.53 Tg, exhibits an increased area under the crystal peaks. The increased area means a more stable material property.

TABLE 1
	Bending		Bending		Bending
	Strength		Strength		Strength
Group 1	(MPa)	Group 2	(MPa)	Group 3	(MPa)
A1	1978.15	B1	2695.73	C1	965.02
A2	1645.26	B2	2681.6	C2	644.58
A3	1768.73	B3	2282.61	C3	1248.12
A4	1471.5	B4	2362.84	C4	683.6
A5	2280.92	B5	2482.1	C5	621.37
Average	1828.912	Average	2500.976	Average	832.538
Variance	333.7656	Variance	150.1512	Variance	219.2256

In the second embodiment, high purity (purity is greater than 99.0wt %) Zr, Ti, Cu, Ni and Be with a weight ratio corresponding to the composition of Zr₄₁Ti₁₄Cu₁₅Ni₁₀Be₂₀ were melted in an electrical arc furnace. Subsequently, a copper mould was used for die casting in the presence of a protective Argon gas. The die casting was performed under a pressure of 120 Pa and with a casting speed of 4 m/s. Fifteen amorphous alloy die casts were prepared for experimental purposes, each having a size of 80 mm×18 mm×1 mm. The fifteen amorphous alloy die casts were transition temperature Tg was determined to be 662K for this type of alloy by performing a DSC test. The fifteen die casts were divided into three groups.

The first group includes D1 to D5, all of which were not subjected to any aging treatments.

The second group includes D6 to D10, each of which was subjected to an aging treatment in an atmospheric pressure of 0.1 MPa, at a temperature of 0.57 Tg (377K) , for a time period of 0.5 hour. The resulted die casts were labeled as E1 to E5.

The third group includes D11 to D15, each of which was subjected to an aging treatment under a pressure of 0.1 MPa, at a temperature of 0.47 Tg (311 K) , for a time period of 0.5 hour. The resulted die casts were labeled as F1 to F5.

Property Test

Bending resistance strength test was performed on the 3 groups of die casts.

Pursuing to standard bending resistance test disclosed in GB/T14452-93 and using a CMT5105 universal material testing machine, the three-point bending fracturing tests were performed on each of the die casts groups D1-D5, E1-E5, and F1-F5. The resulted strength values were recorded. The average and variance of the strength values were calculated. All data are shown in Table 2.

TABLE 2
	Bending		Bending		Bending
	Strength		Strength		Strength
Group 1	(MPa)	Group 2	(MPa)	Group 3	(MPa)
D1	2077.9	E1	2321.8	F1	2184.69
D2	1937.27	E2	2423.4	F2	2023.29
D3	1606.07	E3	2845.43	F3	1721.34
D4	1715.41	E4	2343.16	F4	1763.76
D5	1660.24	E5	2275.54	F5	2107.59
Average	1799.378	Average	2441.866	Average	1960.134
Variance	338.1664	Variance	161.4256	Variance	300.6715

Conclusion of the Experiments

Referring to Table 1, it is shown that die casts B1-B5, which were subjected to an aging treatment at a temperature of 0.53 Tg, have better bending resistance and stability in comparison with die casts A1-A5, which were not subjected to aging treatments, and C1-C5, which subjected to an aging treatment at a temperature of 0.81 Tg. Referring to Table 2, die casts E1-E5 have improved bending resistance and stability, in comparison with die casts D1-D5, which were not subjected to any aging treatments, and die casts F1-F5, which were subjected to aging treatments under a temperature of 0.47 Tg.

In this specification, the terms “one embodiment,” “some embodiments,” “exemplary embodiment,” “specific exemplary embodiment,” or “some exemplary embodiments” mean that the described specific characteristics, structures, materials or features based on the underlining embodiments exist in at least one of the embodiments or exemplary embodiments. However, in this specification, an exemplary description associated with the above terms does not necessarily mean the same embodiment. In addition, the described specific characteristics, structures, materials or features may be properly combined in one or more embodiments or exemplary embodiments.

Although explanatory embodiments have been shown and described, it would be appreciated by those skilled in the art that changes, alternatives, and modifications all falling into the scope of the claims and their equivalents may be made in the embodiments without departing from spirit and principles of the present disclosure.

Claims

1. A heat treatment process for an amorphous alloy die cast comprising:

subjecting the amorphous alloy die cast to an aging treatment at a temperature of about 0.5 Tg to about 0.6 Tg, wherein Tg is a glass transition temperature of the alloy, and for a time period of about 10 minutes to about 24 hours.

2. The heat treatment process of claim 1, wherein the temperature is about 0.53 Tg to about 0.57 Tg, and the time period is about 30 minutes to about 60 minutes.

3. The heat treatment process of claim 1, wherein the amorphous alloy die cast is formed by a die casting process in a condition of a pressure of about 50 Pa to about 200 Pa and a die casting speed of about 3 m/s to about 5 m/s.

4. The heat treatment process of claim 1, wherein the amorphous alloy die cast has a thickness of about 0.5 mm to about 2 mm.

5. The heat treatment process of claim 1, wherein the amorphous alloy die cast has a thickness of about 1.0 mm to about 1.5 mm.

6. The heat treatment process of claim 1, wherein the aging treatment is performed under a positive pressure of about 0.1 MPa to about 0.5 MPa.

7. The heat treatment process of any one of claims 1, 3, 4, and 6, wherein the amorphous alloy die cast thereof,

comprises Zr, and

is represented by a formula of (Zr1−xTix)a(Cu1−yNiy)bAlcMd, wherein M is selected from the group consisting of: Be, Y, Sc, La, and combinations

“x” is in the range of from 0 to 0.45 in atomic percentage, “y” is in the range of from 0 to 0.75 in atomic percentage, “a” is in the range of from 38 to 65, “b” is in the range of from 20 to 40, “c” is in the range of from 0 to 15, “d” is in the range of from 0 to 30, and the sum of a, b, c, and d in atomic percentage equals to 100.

8. An amorphous alloy die cast, wherein the amorphous alloy die cast

comprises Zr and

is treated by the heat treatment process described in any one of claims 1, 3, 4, and 6.

9. The amorphous alloy die cast of claim 8, wherein the amorphous alloy die cast is represented by a formula of (Zr1−xTix)a(Cu1−yNiy)bAlcMd, in which

M is selected from the group consisting of: Be, Y, Sc, La, and combinations thereof,

“x” is in the range of from 0 to 0.45,

“y” is in the range of from 0 to 0.75,

“a” is in the range of from 38 to 65,

“b” is in the range of from 20 to 40,

“c” is in the range of from 0 to 15,

“d” is in the range of from 0 to 30, and

the sum of a, b, c, and d in atomic percentage equals to 100.

10. The amorphous alloy die cast of claim 9, wherein the amorphous alloy die cast is represented by a formula of Zr55Al15Cu25Ni5 or Zr41Ti14Cu15Ni10Be20.

11. The amorphous alloy die cast of claim 8, wherein the amorphous alloy die cast has a thickness of about 0.5 mm to about 2 mm.