CN1354274A - Nickel base amorphous alloy - Google Patents
Nickel base amorphous alloy Download PDFInfo
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- CN1354274A CN1354274A CN 00123285 CN00123285A CN1354274A CN 1354274 A CN1354274 A CN 1354274A CN 00123285 CN00123285 CN 00123285 CN 00123285 A CN00123285 A CN 00123285A CN 1354274 A CN1354274 A CN 1354274A
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- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 85
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 38
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 17
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 43
- 239000000956 alloy Substances 0.000 claims abstract description 43
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 12
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052718 tin Inorganic materials 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 4
- 229910052745 lead Inorganic materials 0.000 claims abstract description 3
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052703 rhodium Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 16
- 239000000843 powder Substances 0.000 claims description 12
- 238000005275 alloying Methods 0.000 claims description 11
- 239000011159 matrix material Substances 0.000 claims description 6
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 3
- 238000007596 consolidation process Methods 0.000 claims description 2
- 238000001816 cooling Methods 0.000 claims description 2
- 238000009826 distribution Methods 0.000 claims description 2
- 239000002105 nanoparticle Substances 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims 1
- 238000002425 crystallisation Methods 0.000 abstract description 17
- 230000008025 crystallization Effects 0.000 abstract description 17
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 230000009477 glass transition Effects 0.000 abstract description 3
- 229910052710 silicon Inorganic materials 0.000 abstract description 3
- 229910052790 beryllium Inorganic materials 0.000 abstract description 2
- 229910052763 palladium Inorganic materials 0.000 abstract description 2
- 229910052777 Praseodymium Inorganic materials 0.000 abstract 1
- 238000006243 chemical reaction Methods 0.000 abstract 1
- 239000007788 liquid Substances 0.000 abstract 1
- 238000004781 supercooling Methods 0.000 abstract 1
- 239000010936 titanium Substances 0.000 description 39
- 239000013526 supercooled liquid Substances 0.000 description 20
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 16
- 238000005551 mechanical alloying Methods 0.000 description 10
- 239000000203 mixture Substances 0.000 description 10
- 239000007789 gas Substances 0.000 description 9
- 229910052786 argon Inorganic materials 0.000 description 8
- 239000005300 metallic glass Substances 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 6
- 238000004458 analytical method Methods 0.000 description 5
- 238000000498 ball milling Methods 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 229910052719 titanium Inorganic materials 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 238000007731 hot pressing Methods 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 229910002058 ternary alloy Inorganic materials 0.000 description 4
- 229910001093 Zr alloy Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 239000011521 glass Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000001228 spectrum Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910017755 Cu-Sn Inorganic materials 0.000 description 1
- 229910017927 Cu—Sn Inorganic materials 0.000 description 1
- 229910018104 Ni-P Inorganic materials 0.000 description 1
- 229910018536 Ni—P Inorganic materials 0.000 description 1
- 229910001096 P alloy Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 description 1
- 239000003963 antioxidant agent Substances 0.000 description 1
- 230000003078 antioxidant effect Effects 0.000 description 1
- 235000006708 antioxidants Nutrition 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
The present invention relates to a nickel base amorphous alloy, its basic components (at.%) are NiA Tib Zrc, here a=50-70, b=1-25 and c=100-a-b. The Ni element can be substituted with one or several elements of Cu, Co, Fe, Sn, MO, Cr,Mn, Nb, W or Pd. Zr can be substituted with one or several elements of Hf, Nb, Ta, Mo, W or Pr. Ti can be substituted with one or several elements of Al, Mg, Sn, Ag, Hf, Nb, Pb, Pr, Sb, Rh, Be, P, B, C or Si. Said alloy possesses good intrinsic amorphous forming capacity and thermal stability. before producing crystallization conversion, said amorphous structure possesses obvious glass-transition so as to form wide supercooling liquid state temp. interval.
Description
The present invention relates to the amorphous alloy in the metallic substance, have the new amorphous state nickel-base alloy of broad supercooled liquid temperature range (more than 50 ℃).
Compare with conventional polycrystalline metal material, amorphous alloy (also claiming metallic glass) is because the long-range of structure is unordered and do not have crystal boundary, therefore has characteristics such as high strength and toughness is corrosion-resistant and anti-oxidant.Some amorphous alloys are taking place to have tangible glass transition before the crystallization change, and (Δ T is defined as the starting temperature T that crystallization takes place in the continuous heat-processed of non-crystalline state to show the supercooled liquid temperature range Δ T of broad
xWith glass transformation temperature T
gDifference), the size of Δ T value has become one of important criterion of weighing amorphous alloy intrinsic amorphous formation ability and thermostability.Have now found that manyly form amorphous alloy system and have above-mentioned feature, Δ T value can be above 50 ℃, even surpass 100 ℃, as Mg-Ln-TM, Ln-Al-TM, Zr-Al-TM, Ti-Zr-TM, Zr-(Ti, Nb, Pd)-and Al-TM, Zr-Ti-TM-Be, Fe-(Al, Ga)-(P, C, B, Si), Pd-Cu-Ni-P, (Fe, Co)-(Zr, Hf, Nb, Ta)-B and Ti-Ni-Cu-Sn (Ln=lanthanide series metal, TM=magnesium-yttrium-transition metal) etc.Another characteristics of this class alloy are: amorphous alloy shows as densify fluid in supercooled liquid temperature range Δ T, has superplasticity, its unit elongation even can reach 15,000%.Utilize this characteristic can realize the near clean shape processing of non-crystaline amorphous metal, be made into complex-shaped small-sized component.Therefore, the supercooled liquid temperature range Δ T of amorphous alloy broad and the characteristic of in Δ T temperature range, hanging down viscosity factor, not only the following process moulding for amorphous alloy provides chance, also makes simultaneously to be consolidated into block materials by amorphous alloy powder or strip through powder metallurgy technology and to be easy to realize.
Usually, nickel base amorphous alloy has better magnetic properties, anticorrosive and oxidation susceptibility and high intensity and wear resistance.Although existing ni-based amorphous alloy Ni-M-(P, Si, B, the C) research of (M=Al, Ti, Zr, Cr, Mo, W) report does not find almost that at present performance has tangible supercooled liquid temperature range in the Ni base noncrystal alloy.Recently, Japan Akihisa Inoue people such as (A.Inoue) has studied Ni-(Ti, Nb)-amorphous formation ability of P alloy system, and adopt melt to inhale the amorphous bar that casting process has obtained diameter 2mm, but the crystallization temperature of non-crystaline amorphous metal lower (about 350 ℃), supercooled liquid temperature range also narrower (about 40 ℃).
The object of the present invention is to provide a kind of nickel base amorphous alloy, this alloy has broad supercooled liquid temperature range.
The invention provides a kind of nickel base amorphous alloy, it is characterized in that basal component is atomic percent: Ni50～70Ti1～25Zr surplus.
Element Ni among the present invention can be substituted simultaneously by any alloying element among Cu, Co, Fe, Sn, Mo, Cr, Mn, Nb, W or the Pd or multiple alloying element, and the amount of substituting is less than 30% of alloy total amount; Element Zr wherein can be substituted simultaneously by any alloying element among Hf, Nb, Ta, Mo, W or the Pr or multiple alloying element, and the amount of substituting is less than 15% of alloy total amount; Element ti wherein can be by any metal among Al, Mg, Sn, Ag, Hf, Nb, Pb, Pr, Sb, Rh or the Be, or any non-metallic element among P, B, C, the Si, or multiple alloying element substitutes simultaneously, and the amount that substitutes is for less than 20% of alloy total amount.
Nickel base amorphous alloy described in the present invention comprises powder, filament, strip or block materials.
Nickel base amorphous alloy described in the present invention can form matrix material or the bulk nanometer material that contains interior living disperse distribution nano particle/amorphous alloy matrix by the speed of cooling of control melt or the consolidation temperature of amorphous alloy powder.
Nickel base amorphous alloy described in the present invention can develop into structures such as nanocrystalline, crystallite through subsequent disposal.
The key that the present invention is different from the existing Ni-based alloy of non-crystalline state is: alloy can be observed tangible glass transition and has the supercooled liquid temperature range Δ T of broad (generally more than 50 ℃, the highest can near 100 ℃) before crystallization takes place.Simultaneously, the alloy that forms amorphous structure has higher crystallization temperature (generally more than 550 ℃), and the thermostability of the Ni-based alloy of non-crystalline state and working temperature are improved significantly and improve.
The present invention is by Ni-Ti-Zr ternary alloy amorphous formation ability and Research on Thermal Stability to the heterogeneity proportioning, several new amorphous state nickel-base alloys have been found with broad supercooled liquid temperature range (more than 50 ℃), the intrinsic amorphous formation ability of alloy is stronger, can be by some preparation of more common method and production.Can also this prepare the novel material of the metastable state structure of deriving out, such as with matrix material and the nanocrystalline Ni-based alloy of the Ni-based alloy of non-crystalline state as matrix by the Ni-based alloy of non-crystalline state for the basis.
Accompanying drawing 1 forms Ni for mechanical alloying after 40 hours
X(Ti
0.5Zr
0.5)
100-XThe X ray diffracting spectrum of (X=10,20,33.3,40,50,55,60,65,70,80,90) powdered alloy.
The non-crystalline state Ni that accompanying drawing 2 mechanical alloyings formed after 40 hours
X(Ti
0.5Zr
0.5)
100-XThe dsc analysis result of (X=33.3,40,50,55,60,65,80) powdered alloy (heating rate is 40K/min).
The non-crystalline state Ni that accompanying drawing 3 mechanical alloyings formed after 40 hours
60Ti
XZr
40-XThe dsc analysis result of (X=0,10,20,25,30,35,40) powdered alloy (heating rate is 40K/min).
Accompanying drawing 4 contains dsc analysis result (a) Ni of the non-crystalline state Ni-Ti-Zr alloy of Co P
76Ti
5P
19(b) Ni
60Ti
20Zr
20(c) Ni
30Co
30Ti
17.5Zr
17.5P
5And (d) Ni
30Co
30Ti
15Zr
15P
10(heating rate is 40K/min).
Accompanying drawing 5 fast quenching amorphous attitude Ni
60Ti
20Zr
20The dsc analysis result (heating rate is 40K/min) of alloy strip (a) and mechanical alloying amorphous alloy powder (b).
Accompanying drawing 6 Ni
50Co
8Cr
2Ti
5Zr
20P
15The non-crystaline amorphous metal block materials that the non-crystalline state powder obtains after the fixed moulding of hot pressing (diameter 20mm, height 13mm).
The diameter that accompanying drawing 7 adopts water cooled copper mould to inhale the casting process acquisition is the Ni of 6mm, length 55mm
60Ti
20Zr
20Bulk amorphous alloy.
The embodiment of the invention is as follows:
Embodiment 1
Adopt US-built Spex-8000 type high-energy ball mill about 40 microns Ni (99.5wt%) of ball milling particle diameter under high-purity argon gas (99.999%) protection; Ti (99.6wt%); Zr (99.4wt%) ternary powder mixture; ball is 81 with the weight of material ratio; milling time is 20～50 hours, finally is formed into to be divided into Ni
X(Ti
0.5Zr
0.5)
100-XThe powdered alloy of (X=10,20,33.3,40,50,55,60,65,70,80,90), the X-ray diffraction spectrum of different-alloy and heat are analyzed (DSC) result respectively as depicted in figs. 1 and 2.The result shows: Ni content can be completed into amorphous phase at the mixed powder of 20≤x≤80 after mechanical alloying in 40 hours, but only there is the tangible supercooled liquid temperature range more than 50 ℃ in the composition range amorphous phase in 50≤x≤65, and the maximum value of non-crystaline amorphous metal supercooled liquid temperature range is near 100 ℃; Composition range at the crystallization temperature of the Ni-based alloy of non-crystalline state of 50≤x≤65 all more than 550 ℃.Glass transformation temperature (the T of ternary Ni-Ti-Zr alloy
g), crystallization starting temperature (T
x) and supercooled liquid temperature province width (Δ T) list in table 1.
Table 1 mechanical alloying forms the glass transformation temperature (T of ternary Ni-Ti-Zr amorphous alloy
g), crystallization starting temperature (T
x) and supercooled liquid temperature range (Δ T) (heating rate of DSC is 40 ℃/minute)
| Alloy | ????T g(℃) | ????T x(℃) | ????ΔT(℃) |
| ??Ni 50Ti 25Zr 25 | ????482 | ????533 | ????51 |
| ??Ni 55Ti 22.5Zr 22.5 | ????494 | ????561 | ????67 |
| ??Ni 60Ti 20Zr 20 | ????437 | ????516 | ????79 |
| ??Ni 65Ti 17.5Zr 17.5 | ????434 | ????484 | ????50 |
Embodiment 2
Adopt US-built Spex-8000 type high-energy ball mill about 40 microns Ni (99.5wt%) of ball milling particle diameter under high-purity argon gas (99.999%) protection; Ti (99.6wt%); Zr (99.4wt%) ternary powder mixture; ball is 81 with the weight of material ratio; milling time is 20～50 hours, is formed into to be divided into Ni
60Ti
XZr
40-XThe powdered alloy of (X=0,10,20,25,30,35,40).Ni
60Ti
XZr
40-XAlloy all can form amorphous phase in the scope of X=0～40, but only there is the tangible supercooled liquid temperature range more than 50 ℃ in the composition range amorphous phase in 0≤x≤25, the maximum value of amorphous alloy supercooled liquid temperature range is near 100 ℃, as shown in Figure 3, the crystallization temperature of the Ni-based alloy of non-crystalline state is all more than 580 ℃.Glass transformation temperature (the T of ternary Ni-Ti-Zr alloy
g), crystallization starting temperature (T
x) and supercooled liquid temperature province width (Δ T) list in table 2.
Glass transformation temperature (the T of the ternary Ni-Ti-Zr amorphous alloy that table 2 mechanical alloying forms
g), crystallization starting temperature (T
x) and supercooled liquid temperature range (Δ T) (heating rate of DSC is 40 ℃/minute)
| Alloy | ????T g(℃) | ????T x(℃) | ????ΔT(℃) |
| ????Ni 60Zr 40 | ????445 | ????488 | ????43 |
| ????Ni 60Ti 5Zr 35 | ????442 | ????520 | ????78 |
| ????Ni 60Ti 10Zr 30 | ????458 | ????513 | ????55 |
| ????Ni 60Ti 15Zr 25 | ????514 | ????564 | ????50 |
Embodiment 3
Adopt US-built Spex-8000 type high-energy ball mill about 40 microns Ni (99.5wt%) of ball milling particle diameter under high-purity argon gas (99.999%) protection; Co (99.8wt%); Ti (99.6wt%); the ternary of Zr (99.4wt%) and P (99.999wt%) or polynary powder mixture, the weight ratio of ball and material are 8: 1.By Ni Zr and Ti in alloying element Co and the partly alternative Ni-Ti-Zr ternary alloy of P, the powdered alloy heat of formation is analyzed (DSC) and be the results are shown in Figure 4.Provided the Ni that forms by mechanical alloying among the figure simultaneously
76Ti
5P
19The result of (A.Inoue composition) amorphous alloy powder is to contrast.The result shows: the Ni-Ti-Zr ternary alloy has better thermostability (being higher crystallization temperature) than the Ni-Ti-P ternary alloy; Partly substitute Ni, partly substitute the thermostability that Ti can further improve Ni-Ti-Zr ternary non-crystaline amorphous metal with Co with P.Table 3 is listed the crystallization starting temperature value (T of the Ni-based alloy of above-mentioned non-crystalline state
x).
Crystallization starting temperature (the T of the Ni-based alloy of several mechanical alloying non-crystalline states of table 3
x)
| Alloy | ??T x(℃) |
| ??Ni 76Ti 5P 19 | ????348 |
| ??Ni 60Ti 20Zr 20 | ????520 |
| ??Ni 30Co 30Ti 17.5Zr 17.5P 5 | ????552 |
| ??Ni 30Co 30Ti 15Zr 15P 10 | ????566 |
Embodiment 4
With commercially available technical pure Ni (99.5wt%), Ti (99.6wt%) and sponge Zr (99.4wt%) parent material are pressed Ni
60Ti
20Zr
20Atomic percent configuration alloy 100 grams, in electric arc furnace, charge into high purity argon (99.999%) repeatedly refining obtain master alloy ingot 4 times.Adopt single roller melt supercooled technology spray to cast under low pressure high-purity argon atmosphere to become strip, strip is wide 5 millimeters, thick 40 microns.Table 4 is the main control parameters of melt-spun.The dsc analysis result of amorphous alloy band as shown in Figure 5.By
Table 4 melt-spun prepares Ni
60Ti
20Zr
20The amorphous alloy main technical details
Scheme as seen the Ni that chilling forms
60Ti
20Zr
20Amorphous alloy band crystallization temperature and supercooled liquid temperature range are lower than the composition alloy of the same race of mechanical alloying method preparation among the embodiment 1, but the supercooled liquid interval of amorphous ribbon still reaches 76 ℃, and crystallization temperature is 570 ℃.
| The fast quenching roller speed | ????30m/s |
| The melt jet temperature | ????1350℃ |
| The silica tube nozzle diameter | ????0.6mm |
| Spraying pressure | ????+0.5atm |
| Furnace pressure | ????200mmHg |
| Crucible nozzle/wheel | ????3mm |
| Furnace gas | ????Ar(99.999％) |
Embodiment 5
Adopting the homemade planetary high-energy ball mill of WL-1 type about 40 microns composition proportion of ball milling particle diameter under high-purity argon gas (99.999%) protection is Ni
50Co
8Cr
2Ti
5Zr
20P
15The Ni of (atomic percent) (99.5wt%), hexa-atomic powdered mixture 180 grams of Co (99.8wt%), Cr (99.9wt%), Ti (99.6wt%), Zr (99.4wt%) and P (99.999wt%), the weight ratio of ball and material is 15: 1.Ball milling obtains the powdered alloy of complete amorphous phase after 40 hours.Ball grinder is opened (avoiding exposing air) at the gloves that are filled with high-purity argon gas in mutually, will fill in after the powder collection in the cold stamping die, and at room temperature to be pressed into blank under the pressure of about 100MPa in advance, good compactness is in 70%.The blank of will colding pressing is put into hot pressing die, in installation and the vacuum hotpressing device.Device is evacuated to 5.4 * 10
-3Behind the Pa, feed argon gas, be heated to 480 ℃ of press temperatures (press temperature is controlled in the supercooled liquid temperature province of this amorphous alloy), exerting pressure is 2-3GPa, about 10 minutes of soaking time.Form relative density after the hot pressing and be better than 99% non-crystaline amorphous metal block materials, the exterior appearance of material is seen Fig. 6.
Embodiment 6
With commercially available high-purity N i (99.995wt%), Ti (99.996wt%), Zr (99.95wt%) sheet material or bar is raw material, presses Ni
60Ti
20Zr
20Atomic percent configuration alloy 12 grams; in the direct current arc smelting furnace of titanium gas collection is arranged, charge into high-purity argon gas (99.999%) repeatedly after the refining 8 times, adopt water cooled copper mould piston suction casting method to obtain part amorphous phase alloy bar material Fig. 7 of 6 millimeters of diameters, 55 millimeters of length.
Claims (7)
1, a kind of nickel base amorphous alloy is characterized in that basal component is atomic percent:
Ni50～70Ti1～25Zr surplus.
2, according to right 1 described nickel base amorphous alloy, it is characterized in that element Ni part is wherein substituted simultaneously by any alloying element among Cu, Co, Fe, Sn, Mo, Cr, Mn, Nb, W or the Pd or multiple alloying element, the amount of substituting is less than 30% of alloy total amount.
3, according to right 1 described nickel base amorphous alloy, it is characterized in that the element Zr part in the element is wherein substituted simultaneously by any alloying element among Hf, Nb, Ta, Mo, W or the Pr or multiple alloying element, the amount of substituting is less than 15% of alloy total amount.
4, according to right 1 described nickel base amorphous alloy, it is characterized in that element ti part in the element wherein is by any metal among Al, Mg, Sn, Ag, Hf, Nb, Pb, Pr, Sb, Rh or the Be, or any non-metallic element among P, B, C, the Si, or multiple alloying element is alternative simultaneously, and the amount of substituting is less than 20% of alloy total amount.
5,, it is characterized in that described nickel base amorphous alloy comprises powder, filament, strip or block materials according to right 1,2,3 or 4 described nickel base amorphous alloys.
6,, it is characterized in that forming matrix material or the bulk nanometer material that contains interior living disperse distribution nano particle/amorphous alloy matrix by the speed of cooling of control melt or the consolidation temperature of amorphous alloy powder according to the nickel base amorphous alloy of right 1,2,3 or 4 described chemical ingredientss.
7,, it is characterized in that developing into nanocrystalline, microlitic structure through subsequent disposal according to right 1,2,3 or 4 described nickel base amorphous alloys.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB001232851A CN1142313C (en) | 2000-11-22 | 2000-11-22 | Nickel base amorphous alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB001232851A CN1142313C (en) | 2000-11-22 | 2000-11-22 | Nickel base amorphous alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1354274A true CN1354274A (en) | 2002-06-19 |
| CN1142313C CN1142313C (en) | 2004-03-17 |
Family
ID=4589743
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB001232851A Expired - Fee Related CN1142313C (en) | 2000-11-22 | 2000-11-22 | Nickel base amorphous alloy |
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| Country | Link |
|---|---|
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Cited By (38)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1332056C (en) * | 2005-06-07 | 2007-08-15 | 山东大学 | Copper-base amorphous alloy and its preparing proess |
| CN100429329C (en) * | 2007-02-09 | 2008-10-29 | 浙江大学 | Ni-Nb-Zr-Co bulk amorphous alloy |
| CN100513021C (en) * | 2004-08-04 | 2009-07-15 | 同和电子科技有限公司 | Powder of fine alloy particles having an uneven surface and method of manufacturing the powder |
| US7591910B2 (en) * | 2002-12-04 | 2009-09-22 | California Institute Of Technology | Bulk amorphous refractory glasses based on the Ni(-Cu-)-Ti(-Zr)-Al alloy system |
| CN101451223B (en) * | 2007-11-30 | 2010-08-25 | 比亚迪股份有限公司 | Zirconium based amorphous alloy and manufacture method thereof |
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-
2000
- 2000-11-22 CN CNB001232851A patent/CN1142313C/en not_active Expired - Fee Related
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