CN116623107B - Zr-based bulk amorphous alloy with excellent compression plasticity and preparation method thereof - Google Patents
Zr-based bulk amorphous alloy with excellent compression plasticity and preparation method thereof Download PDFInfo
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- CN116623107B CN116623107B CN202310608794.9A CN202310608794A CN116623107B CN 116623107 B CN116623107 B CN 116623107B CN 202310608794 A CN202310608794 A CN 202310608794A CN 116623107 B CN116623107 B CN 116623107B
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- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 51
- 230000006835 compression Effects 0.000 title claims abstract description 34
- 238000007906 compression Methods 0.000 title claims abstract description 34
- 238000002360 preparation method Methods 0.000 title abstract description 7
- 238000005266 casting Methods 0.000 claims abstract description 21
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052802 copper Inorganic materials 0.000 claims abstract description 18
- 239000010949 copper Substances 0.000 claims abstract description 18
- 238000002844 melting Methods 0.000 claims abstract description 9
- 230000008018 melting Effects 0.000 claims abstract description 9
- 239000010936 titanium Substances 0.000 claims description 71
- 229910045601 alloy Inorganic materials 0.000 claims description 53
- 239000000956 alloy Substances 0.000 claims description 53
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 26
- 238000003723 Smelting Methods 0.000 claims description 17
- 229910052786 argon Inorganic materials 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 13
- 239000000126 substance Substances 0.000 claims description 11
- 238000010891 electric arc Methods 0.000 claims description 7
- 239000007788 liquid Substances 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 238000001816 cooling Methods 0.000 claims description 3
- 238000005516 engineering process Methods 0.000 claims description 3
- 239000000155 melt Substances 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 239000007787 solid Substances 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims 4
- 238000005086 pumping Methods 0.000 claims 1
- 238000012545 processing Methods 0.000 abstract description 7
- 238000005728 strengthening Methods 0.000 abstract description 7
- 238000000034 method Methods 0.000 abstract description 5
- 229910000831 Steel Inorganic materials 0.000 abstract description 4
- 239000010959 steel Substances 0.000 abstract description 4
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 238000010008 shearing Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 3
- 239000013079 quasicrystal Substances 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000012669 compression test Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 2
- 229910010271 silicon carbide Inorganic materials 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000011089 mechanical engineering Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/10—Amorphous alloys with molybdenum, tungsten, niobium, tantalum, titanium, or zirconium or Hf as the major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D18/00—Pressure casting; Vacuum casting
- B22D18/06—Vacuum casting, i.e. making use of vacuum to fill the mould
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/11—Making amorphous alloys
Abstract
The invention discloses a Zr-based bulk amorphous alloy with excellent compression plasticity and a preparation method thereof, wherein the molecular formula of the Zr-based bulk amorphous alloy is ((Zr) 40 Ti 40 Ni 20 ) 100‑x Be x ) 100‑y Nb y Wherein x is more than or equal to 20 and less than or equal to 28,0, y is more than or equal to 12; by forming a bulk amorphous alloy system (Zr 40 Ti 40 Ni 20 ) 100‑x Be x (x is more than or equal to 20 and less than or equal to 28) and directly obtaining the Zr-based bulk amorphous alloy by adopting an arc melting and copper mold suction casting method; the compression plasticity of three components in the Zr-based bulk amorphous alloy prepared by the invention is more than 25%, and the optimal component ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 The compression plasticity of the steel is as high as 29.7%, and the steel shows remarkable processing strengthening behavior with yield strength of 1985MPa and maximum compressive strength of 2818.7 MPa.
Description
Technical Field
The invention belongs to the technical field of amorphous alloy, and particularly relates to Zr-based bulk amorphous alloy with excellent compression plasticity and a preparation method thereof.
Background
The bulk amorphous alloy has the structural characteristics of long-range disordered short-range order, so that the bulk amorphous alloy has a plurality of unique and excellent physical and chemical properties. The zirconium-based amorphous alloy has remarkable application prospect in various fields such as sports equipment, mechanical engineering and the like due to the characteristics of large critical dimension, high strength, elastic strain, relatively low elastic modulus and the like. However, amorphous alloys do not have defects such as grain boundaries, dislocation and the like, and are low in room-temperature plasticity and often show brittle fracture, which severely limits the practical application range. Therefore, zr-based bulk amorphous alloys with high plasticity and high strength are always the goal pursued by scientists.
Disclosure of Invention
The invention aims to provide a Zr-based bulk amorphous alloy with excellent compression plasticity and a preparation method thereof. The invention is mainly characterized in that a bulk amorphous alloy system (Zr 40 Ti 40 Ni 20 ) 100-x Be x And (x is more than or equal to 20 and less than or equal to 28) is doped with Nb, and the product of the invention is directly obtained by adopting an electric arc melting and copper die suction casting method.
The aim of the invention is achieved by the following scheme:
zr-based bulk amorphous alloy with excellent compression plasticity, and molecular formula of Zr-based bulk amorphous alloy is ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Wherein x is more than or equal to 20 and less than or equal to 28,0, y is more than or equal to 12.
Preferably, x is more than or equal to 24 and less than or equal to 28, and y is more than or equal to 3 and less than or equal to 6.
Preferably, the yield strength, the maximum compressive strength and the plastic strain amount of the Zr-based bulk amorphous alloy all increase and decrease with increasing Nb content.
The invention also provides a preparation method of the Zr-based bulk amorphous alloy with excellent compression plasticity, which comprises the following steps:
(1) Arc melting to prepare alloy ingots:
zr is added into the vacuum arc furnace according to the proportion 40 Ti 40 Ni 20 The mother alloy ingot and Be simple substance are vacuumized before smelting alloy, and the vacuum degree reaches 6 multiplied by 10 -4 During Pa, high-purity argon is filled to the pressure of 0.2 multiplied by 10 in the furnace chamber of the electric arc furnace 5 Pa, then smelting for five times under the protection of argon, wherein the smelting current is 200-240 amperes, and cooling in a water-cooled copper crucible after all solid substances are smelted into liquid to obtain (Zr) with uniform components 40 Ti 40 Ni 20 ) 100-x Be x Master alloy, x is more than or equal to 20 and less than or equal to 28;
(Zr) with the compression plasticity of more than 10 percent in proportion 40 Ti 40 Ni 20 ) 100-x Be x Adding Nb simple substance into master alloy, adopting and preparing (Zr 40 Ti 40 Ni 20 ) 100-x Be x The mother alloy is smelted for five times under the same operation conditions and steps to obtain ((Zr) with uniform components 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y An alloy ingot, wherein y is more than or equal to 0 and less than or equal to 12;
(2) The Zr-based bulk amorphous alloy is obtained by copper mold suction casting technology:
will ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Placing the alloy ingot into a copper molten pool of copper mold suction casting equipment, vacuumizing the equipment, and waiting for the vacuum degree to reach 6 x 10 -4 During Pa, high-purity argon is filled to the pressure of 0.2x10 in the furnace chamber of the electric arc furnace 5 Pa, smelting under the protection of argon, wherein the smelting current is 200-240 amperes, and when the temperature of the melt is 1100-1300 ℃, the melt is ((Zr) 40 Ti 40 Ni 20 ) 100- x Be x ) 100-y Nb y And melting the alloy ingot to liquid, opening a suction casting valve, and sucking the alloy melt into a copper mold to obtain the Zr-based bulk amorphous alloy.
Preferably, before smelting in the step (1) or before suction casting in the step (2), after vacuumizing the equipment and filling high-purity argon, the titanium ingot is firstly melted to absorb the residual oxygen content in the furnace, and then smelting or suction casting is carried out.
Preferably, (Zr) 40 Ti 40 Ni 20 ) 100-x Be x The master alloy has the composition range of24≤x≤28。
Preferably, ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y The composition range of the alloy ingot is more than or equal to 24 and less than or equal to 28, and y is more than or equal to 3 and less than or equal to 6.
Compared with the prior art, the invention has the following advantages and characteristics:
according to the invention, elements Be and Nb are added into an icosahedron quasicrystal system, and a copper die suction casting method is adopted to directly prepare the Zr-based bulk amorphous alloy with high strength, high compression plasticity and obvious processing strengthening characteristics, so that a subsequent treatment process is not needed, and the preparation process is simple; the group of Zr-based bulk amorphous alloys has 3 components with compression plastic deformation exceeding 25%, the optimal components with compression plastic deformation up to 29.7%, and shows remarkable processing strengthening behavior with yield strength of 1985MPa and maximum compressive strength up to 2818.7 MPa.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention, wherein:
FIG. 1 shows as-cast ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y 2-12mm wedge specimen and suction casting cylinder specimen with 16mm and 20mm diameter;
FIG. 2 (a) shows alloy samples ((Zr) with different suction casting diameters 40 Ti 40 Ni 20 ) 76 Be 24 ) 100-y Nb y An XRD pattern of (a); (b) Alloy samples ((Zr) for different suction casting diameters 40 Ti 40 Ni 20 ) 72 Be 28 ) 100-y Nb y An XRD pattern of (a);
FIG. 3 shows a suction casting diameter of 2mm ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Uniaxial compressive stress strain curve of amorphous alloy sample;
FIG. 4 shows the distribution of shear bands on the measured surface of the amorphous alloy rod after compression, and the insert shows the macroscopic morphology of the corresponding sample. Wherein in FIG. 4 (a)The alloy component is Zr 40 Ti 40 Ni 20 ) 72 Be 28 In FIG. 4 (b), the alloy composition ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 In FIG. 4 (c), the alloy composition ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 In FIG. 4 (d), the alloy composition ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 88 Nb 12 ；
Fig. 5 is a composition distribution of an experimentally tested amorphous alloy sample. Wherein, the quasicrystal is formed into a system Zr 40 Ti 40 Ni 20 Considered as a component, denoted by ZTN.
Detailed Description
The following disclosure provides many different embodiments, or examples, for implementing different aspects of the invention. In order to simplify the present disclosure, specific examples are described below. They are, of course, merely examples and are not intended to limit the invention. Furthermore, the present invention may repeat reference numerals and/or letters in the various examples, which are for the purpose of brevity and clarity, and which do not themselves indicate the relationship between the various embodiments and/or arrangements discussed.
The invention selects an alloy system (Zr) with the compression plasticity of more than 10 percent 40 Ti 40 Ni 20 ) 100-x Be x (20.ltoreq.x.ltoreq.28), e.g. (Zr) 40 Ti 40 Ni 20 ) 76 Be 24 And (Zr) 40 Ti 40 Ni 20 ) 72 Be 28 The Zr-based bulk amorphous alloy with compression plasticity obviously superior to that of most of amorphous systems is obtained by doping the Zr-based bulk amorphous alloy with metal Nb.
The materials used in the experiment of the invention are all metal elements with high purity (99.99%).
The following is followed to prepare ((Zr) 40 Ti 40 Ni 20 ) 76 Be 24 ) 94 Nb 6 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 The present invention will be described in detail by taking Zr-based bulk amorphous alloy as an example.
According to Zr 40 Ti 40 Ni 20 Mixing the required simple substance raw materials, adding into a vacuum arc furnace, vacuumizing the equipment until the vacuum degree reaches 6×10 before smelting alloy -4 During Pa, high-purity argon is filled to the pressure of 0.2 multiplied by 10 in the furnace chamber of the electric arc furnace 5 Pa, then smelting the raw materials for five times under the protection of argon, wherein the smelting current is 200-240 amperes, and cooling in a water-cooled copper crucible after all solid substances are smelted into liquid to obtain Zr as the component 40 Ti 40 Ni 20 Is a master alloy ingot; then adding Be simple substance into a vacuum arc furnace according to the proportion, adopting and preparing Zr 40 Ti 40 Ni 20 The mother alloy ingot was smelted five times under the same operating conditions and steps to obtain a molten alloy of uniform composition (Zr) 40 Ti 40 Ni 20 ) 100-x Be x A mother alloy ingot, wherein x is more than or equal to 20 and less than or equal to 28;
to compress a master alloy ingot (Zr) with plasticity of more than 10% 40 Ti 40 Ni 20 ) 76 Be 24 And (Zr) 40 Ti 40 Ni 20 ) 72 Be 28 Adding Nb simple substance into a vacuum arc furnace according to the proportion as raw materials, and adopting and preparing (Zr 40 Ti 40 Ni 20 ) 76 Be 24 And (Zr) 40 Ti 40 Ni 20 ) 72 Be 28 The same operating conditions and steps of the master alloy ingot were melted five times (ensuring homogeneity of the as-cast alloy), and the titanium ingot was first melted to absorb the residual oxygen content in the furnace before melting to obtain ((Zr) of homogeneous composition 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y An alloy ingot; placing the alloy ingot into a copper molten pool of copper mold suction casting equipment, vacuumizing the equipment, and waiting for the vacuum degree to reach 6 x 10 -4 During Pa, high-purity argon is filled to the pressure of 0.2x10 in the furnace chamber of the electric arc furnace 5 Pa, smelting the alloy ingot with the smelting current of 200-240 amperes when smeltingThe alloy was melted to liquid at a bulk temperature of 1100-1300 ℃, a suction casting valve was opened, and the alloy melt was sucked into a copper mold to obtain a Zr-based bulk amorphous alloy (2-12 mm wedge-shaped sample and 16mm and 20mm cylinder samples, as shown in FIG. 1).
The as-cast amorphous sample was cut from the suction cast sample using a water-cooled silicon carbide slow saw, and the microstructure of the sample was analyzed by x-ray diffractometry (XRD, D/max-2500/PC). Figure 2 is an XRD pattern of the largest size (critical amorphous size) amorphous alloy obtained under the present laboratory conditions. Experimental results show that the critical amorphous size of all alloy components is above 9.5 mm. A copper mold with the diameter of 2mm is adopted for suction casting of the completely amorphous alloy rod for mechanical property test.
And adopting a universal testing machine (Instron-5982) to carry out uniaxial compression test on the amorphous alloy sample, and testing the mechanical properties of the amorphous alloy sample. A sample with the length-diameter ratio of 2:1 is intercepted by a water-cooled silicon carbide slow saw from a suction casting amorphous rod with the diameter of 2mm, and is used for a uniaxial compression experiment, and the loaded strain rate is set to be 5 multiplied by 10 -4 s -1 . To ensure the reliability of the data, the compression experiment of the amorphous alloy sample of each component was repeated 3 times, and the compressed data was averaged. The stress-strain curve of the compression test is shown in FIG. 3, and the mechanical parameters obtained by the test are shown in Table 1. The results show that all the samples show certain compression plasticity and also show processing strengthening phenomenon. For both sets of amorphous alloy systems ((Zr) 40 Ti 40 Ni 20 ) 76 Be 24 ) 100-y Nb y And ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 100-y Nb y As the Nb content increases, the yield strength, the maximum compressive strength, and the plastic strain amount of the amorphous alloy all increase and decrease. Wherein (((Zr) 40 Ti 40 Ni 20 ) 76 Be 24 ) 94 Nb 6 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 The plastic deformation of the three amorphous alloy samples is 28.6 percent respectively29.7 percent and 26.2 percent, simultaneously, three samples show obvious processing strengthening phenomena, the yield strengths are respectively 1995MPa, 1985MPa and 2114MPa, the maximum compressive strengths are respectively up to 2822.4MPa, 2818.7MPa and 2868.7MPa, the maximum compressive strengths exceed the yield strengths by about 800MPa, and the breaking strengths are respectively 2003.9MPa, 2261.5MPa and 2092.1MPa, thus being a group of block amorphous alloys with high strength and high compression plasticity.
According to the compression experimental result, select (Zr 40 Ti 40 Ni 20 ) 72 Be 28 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 88 Nb 12 Four representative systems were analyzed by SEM for morphology and shear band distribution of the compressed samples, and the results are shown in fig. 4. The results show that Zr 40 Ti 40 Ni 20 ) 72 Be 28 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 All three amorphous alloy samples with high compression plasticity have obvious 'bulging', wherein ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 Complete fracture did not occur, again indicating that it has very excellent compression plasticity. In the side SEM image of the enlarged sample, a pronounced shear band distribution was found, which was slightly less plastic than ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 88 Nb 12 The lateral shearing bands of the other three samples are distributed more densely, the main shearing band and the secondary shearing band are bent in the expansion process, the phenomena of cutting and bifurcation can occur, and simultaneously finer three-stage shearing bands are generated. This is all in line with the typical characteristics of high compression plastic amorphous alloys.
In conclusion, the invention is realized by preparing Zr in an icosahedron quasicrystal system 40 Ti 40 Ni 20 The experimental technology of the added elements Be and Nb prepares a group of Zr-based bulk amorphous alloys with high strength, high compression plasticity and obvious processing strengthening characteristics. The Zr-based bulk amorphous alloy ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Exhibits a certain compressive plastic deformation in the composition range (x.ltoreq. 28,0.ltoreq.y.ltoreq.12), wherein the amorphous alloy composition having the optimal compressive plastic is present in the composition interval ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y (24.ltoreq.x.ltoreq.28, 3.ltoreq.y.ltoreq.6), as shown in FIG. 5. In this component region, experimentally prepared ((Zr) 40 Ti 40 Ni 20 ) 76 Be 24 ) 94 Nb 6 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 、((Zr 40 Ti 40 Ni 20 ) 72 Be 28 ) 94 Nb 6 The compression plasticity of the amorphous alloy of the three components is more than 25%, and the optimal component ((Zr) 40 Ti 40 Ni 20 ) 72 Be 28 ) 97 Nb 3 The compression plasticity of the steel is as high as 29.7%, and the steel shows remarkable processing strengthening behavior with yield strength of 1985MPa and maximum compressive strength of 2818.7 MPa.
Table 1 ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Mechanical properties of amorphous alloys
Other embodiments of the invention will be apparent to those skilled in the art from consideration of the specification and practice of the invention herein. This invention is intended to cover any variations, uses, or adaptations of the invention following, in general, the principles of the invention and including such departures from the present disclosure as come within known or customary practice within the art to which the invention pertains. It is intended that the specification and examples be considered as exemplary only, with a true scope and spirit of the invention being indicated by the following claims.
It will be understood that the invention is not limited to what has been described above and that various modifications and changes may be made without departing from the scope thereof. The scope of the invention is limited only by the appended claims.
Claims (7)
1. A Zr-based bulk amorphous alloy having excellent compression plasticity, characterized in that the molecular formula of the Zr-based bulk amorphous alloy is ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Wherein x is more than or equal to 20 and less than or equal to 28, and y is more than or equal to 3 and less than or equal to 12.
2. The Zr-based bulk amorphous alloy having excellent compression plasticity according to claim 1, wherein the molecular formula is ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y ，24≤x≤28，3≤y≤6。
3. The Zr-based bulk amorphous alloy having excellent compressive plasticity according to claim 1, wherein the yield strength, maximum compressive strength and plastic strain amount of said Zr-based bulk amorphous alloy all rise and then decrease with increasing Nb content.
4. A method for producing the Zr-based bulk amorphous alloy having excellent compression plasticity according to any one of claims 1 to 3, comprising the steps of:
(1) Arc melting to prepare alloy ingots:
zr is added into the vacuum arc furnace according to the proportion 40 Ti 40 Ni 20 Ingot of mother alloy and Be simple substance, meltBefore alloy smelting, the equipment is vacuumized until the vacuum degree reaches 6 multiplied by 10 -4 During Pa, high-purity argon is filled to the pressure of 0.2 multiplied by 10 in the furnace chamber of the electric arc furnace 5 Pa, then smelting for five times under the protection of argon, wherein the smelting current is 200-240 amperes, and cooling in a water-cooled copper crucible after all solid substances are smelted into liquid to obtain (Zr) with uniform components 40 Ti 40 Ni 20 ) 100-x Be x Master alloy, x is more than or equal to 20 and less than or equal to 28;
the (Zr) with the compression plasticity of more than 10 percent is proportioned 40 Ti 40 Ni 20 ) 100-x Be x Adding Nb simple substance into the master alloy, and adopting and preparing the (Zr) 40 Ti 40 Ni 20 ) 100-x Be x The mother alloy is smelted for five times under the same operation conditions and steps to obtain ((Zr) with uniform components 40 Ti 40 Ni 20 ) 100-x Be x)100-y Nb y An alloy ingot, wherein y is more than or equal to 3 and less than or equal to 12;
(2) The Zr-based bulk amorphous alloy is obtained by copper mold suction casting technology:
the ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y Placing the alloy ingot into a copper molten pool of copper mold suction casting equipment, vacuumizing the equipment, and waiting for the vacuum degree to reach 6 x 10 -4 During Pa, high-purity argon is filled to the pressure of 0.2x10 in the furnace chamber of the electric arc furnace 5 Pa, smelting under the protection of argon, wherein the smelting current is 200-240 amperes, and the ((Zr) is carried out when the temperature of a melt is 1100-1300 DEG C 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y And melting the alloy ingot to liquid, opening a suction casting valve, and sucking the alloy melt into a copper mold to obtain the Zr-based bulk amorphous alloy.
5. The method for producing a Zr-based bulk amorphous alloy having excellent compression plasticity according to claim 4, wherein before melting in step (1) or before suction casting of the alloy in step (2), after vacuum-pumping and high purity argon filling in the apparatus, the titanium ingot is melted to absorb the residual oxygen content in the furnace, and then melting or suction casting is performed.
6. The method for producing a Zr-based bulk amorphous alloy having excellent compression plasticity according to claim 4, wherein said (Zr 40 Ti 40 Ni 20 ) 100-x Be x The composition range of the master alloy is more than or equal to 24 and less than or equal to 28.
7. The method for producing a Zr-based bulk amorphous alloy having excellent compression plasticity according to claim 4, wherein said ((Zr) 40 Ti 40 Ni 20 ) 100-x Be x ) 100-y Nb y The composition range of the alloy ingot is more than or equal to 24 and less than or equal to 28, and y is more than or equal to 3 and less than or equal to 6.
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