CN1388264A - Massive amorphous alloy material - Google Patents
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- CN1388264A CN1388264A CN 01118261 CN01118261A CN1388264A CN 1388264 A CN1388264 A CN 1388264A CN 01118261 CN01118261 CN 01118261 CN 01118261 A CN01118261 A CN 01118261A CN 1388264 A CN1388264 A CN 1388264A
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Abstract
The massive amorphous alloy material may be expressed in Zra-[Nb(Ti)1-xTax]b-Cuc-[Ni1-yFey]d-[Be1-zAlz]e -Mgf-Yg, where a is 25-66, b 1-15, c 8-20, d 1-20, e 5-40, f 0-36, g 0-5, x 0-1, y 0-1 and z 0-1. The material contains at least 50% amorphous phase. The material has low cooling rate, large size, high hardness, high heat stability and wide super-cooling liquid phase area expressing good amorphous area forming capacity.
Description
The present invention relates to Condensed Matter Physics and material science, particularly relate to amorphous metal and alloy, be i.e. non-crystaline amorphous metal or metallic glass field.
Metallic glass normally is cooled to the molten metal alloy to solidify formation below the glass transformation temperature and before forming core and crystallization.Common metal and alloy all want crystallization to form crystal when liquid cooled is got off.Yet, had been found that some metal and alloy when rate of cooling is enough fast, the extreme viscid state in the time of when solidifying, can keeping liquid state, thus suppressing crystallization, this rate of cooling need reach p.s. 10 usually
4～10
6The order of magnitude of K.In order to obtain so high rate of cooling, molten metal or alloy can only be sprayed onto on the extraordinary conductive substrate of heat conduction.The alloy of Huo Deing is a non-crystaline amorphous metal like this, but size is very little.Therefore, previously obtd amorphous alloy material all is that molten metal or alloy are ejected into the strip that obtains on the copper roller of high speed rotating, or is cast to the thin slice that obtains in the cold substrate and powder etc.Found non-crystaline amorphous metal recently, so just can utilize lower rate of cooling to suppress crystallization with stronger inhibition crystallizing power.If under very low rate of cooling, can suppress crystallization, then can make larger sized non-crystaline amorphous metal.
It is amorphous ribbon (document 1, W.Klement, R.H.Wilens that Duwez just adopts copper roller quick quenching technique to prepare AuSi as far back as nineteen sixty, and Duwez, Nature, 1960, vol.187, pp869-70), contain subsequently metalloid element (as Si, C, B, Ge, non-crystaline amorphous metal P), particularly ferrous alloy are by big quantity research.But because the amorphous formation ability of most of alloy is very poor, if need be higher than 10 with fast cold preparation
6The rate of cooling of K/s is so the non-crystaline amorphous metal that makes can only be low-dimensional materials dimensionally, as strip, filament, fine powder.Mechanical alloying also once was a method of preparation amorphous powder, and many alloys can change amorphous into by high-energy ball milling, can press amorphous powder in supercooling liquid phase region subsequently and form amorphous block.Yet the density with the block metal glass of this method preparation is relatively poor, and sneaks into other impurity easily.This external irradiation also can make amorphous metalization, as ion implantation etc.What deserves to be mentioned is that the alloy of precious metal element Pt and Pd has higher amorphous formation ability, as PtNiP, PdNiP can pass through B
2O
3Refining repeatedly, obtain diameter 10mm spherical sample (document 2, H.S.Chen, Mater.Sci.Eng., 1976, Vol.23, pp151-54).So obtaining bulk amorphous alloys is the target that scientists is pursued in decades always.
Up to 1989, the Inoue of Japan etc. has found that MgCuY and LaAlNi are that alloy has very high amorphous formation ability (document 3, A.Inoue, T.Zhang, and T.Masumoto, Mater.Trans., JIM, 1989, Vol.30, pp965-72), can prepare millimetre-sized non-crystaline amorphous metal by the copper mold casting, this is to find that first the millimeter level non-crystaline amorphous metal that does not contain precious metal forms system.Alloy systems such as ZrAlNi, ZrAlCu and ZrAlNiCu have been found subsequently again.Succeeded in developing Zr in succession in the U.S. in 1993 and Japan
41Ti
14Cu
12Ni
10Be
23And Zr
65Al
7.5Ni
10Cul
7.5Bulk amorphous alloys (document 4, A.Peker and W.L.Johnson, Appl.Phys.Lett., 1993, Vol.63 PP2342-44), and is used on golf club panel, other precision optical instrument parts, corrosion-resistant vessel, bullet or the armour piercing shot bullet core very soon.Discover that in addition bulk amorphous alloys has the superplastic deformation ability in supercooling liquid phase region, therefore moulding and the processing for alloy provides possibility.
But the formation of non-crystaline amorphous metal always faces a kind of like this difficulty, crystallization always when promptly the alloy melt of high undercooling solidifies.Crystallization is finished by forming core and crystal growing process.In general, the supercooled liquid crystallization is very fast.Form the non-crystaline amorphous metal solid, must be with the mother alloy liquation from temperature of fusion T
mBe cooled to glass transformation temperature T
gBelow and crystallization can not take place.The state of the art that the preparation of the zirconium base bulk-metallic glass of American and Japanese discovery at present requires is very high, the zirconium that needs ultra-high purity, generally be through the district is molten after purifying and ultrahigh vacuum(HHV) (document 5, C.T.Liu, L.Heatherly, D.S.Easton, C.A.Carmicheal, J.H.Schneibel, C.H.Chen, J.L.Wright, M.H.Yoo, J.A.Horton, and A.Inoue, Metallurgical and MaterialsTransaction A, 1998, Vol 29A, pp1811-1820).
The object of the present invention is to provide a series of block non-crystalline alloy materials, can use following formulate: Zr
a-[Nb (Ti)
1-xTa
x]
b-Cu
c-[Ni
1-y-Fe
y]
d-[Be
1-zAl
z]
e-Mg
f-Y
gWherein the variation range of a, b, c, d, e, f, g is: 25＜a＜66,1＜b＜15,8≤c≤20,1＜d＜20,5＜e＜40,0≤f≤36,0≤g＜5; The variation range of x, y, z is: 0≤x≤1,0≤y≤1,0≤z≤1.This material need comprise the glassy phase or the amorphous phase of at least 50% volume percent.The rate of cooling of material of the present invention is low, and size is not less than 1 millimeter in each dimension.
The object of the present invention is achieved like this:
Fig. 1 is the heat content of typical non-crystaline amorphous metal and the curve of temperature, and wherein curve a is the logarithmic curve of temperature and time, and fusing point T is understood in the figure acceptance of the bid
mWith glass transformation temperature T
g, the front end of curve has been represented and has been separated out the given required shortest time of crystal volume fraction.In order to obtain a kind of unordered solid material, alloy must be from cooling down by glass transition more than the fusing point and crystallization not taking place, promptly alloy when fusing point cools down by glass transformation temperature can not with the crystallization curve intersection.Crystallization curve a has represented the crystallization behavior of the non-crystaline amorphous metal that very early time obtains, and its rate of cooling has surpassed 10
5K/s is usually 10
6The order of magnitude of K/s.Curve b is the crystallization curve of the non-crystaline amorphous metal developed afterwards, forms the needed rate of cooling of non-crystaline amorphous metal and has reduced by 1 or 2 even 3 order of magnitude.Curve c is the crystallization curve of the non-crystaline amorphous metal done of the present invention, and required rate of cooling further greatly reduces, and rate of cooling is no more than per second 10
2K.
Can form non-crystaline amorphous metal and only be the first step that obtains bulk amorphous alloys, what people wanted to obtain is non-crystaline amorphous metal and the machinable parts thereof with big three-dimensional dimension.Make block amorphous alloy can carry out processing treatment and keep its integrity, it is deformable just requiring alloy.Non-crystaline amorphous metal only can be near the glass transformation temperature or abovely could experience uniform deformation under added pressure.In addition, crystallization also takes place in this temperature range usually fast.Therefore as shown in Figure 1, each non-crystaline amorphous metal that forms is reheated glass transformation temperature when above, and there is a very narrow humidity province that crystallization does not take place in non-crystaline amorphous metal before crystallization.
Fig. 2 is non-crystaline amorphous metal logarithm synoptic diagram as the temperature and the viscosity of supercooled liquid between fusing point and glass transformation temperature.At glass transformation temperature, the viscosity of alloy is 10
12The pool order of magnitude.In addition, the viscosity of liquid alloy may be less than 1 pool (the about centipoise(unit of dynamic viscosity of the viscosity of water under the room temperature).Can see that by Fig. 2 the viscosity of non-crystaline amorphous metal reduces with the increase of temperature gradually at cold zone when the heating non-crystaline amorphous metal, changes fast then more than glass transformation temperature.5 degrees centigrade of the every increases of temperature, viscosity reduces an order of magnitude.People wish the viscosity of non-crystaline amorphous metal is reduced to 10
5Pool, so that can make its distortion under less power, this just means and amorphous sample is heated to more than the glass transformation temperature.To processing treatment time of non-crystaline amorphous metal should be on several seconds or the longer time order of magnitude so that have the competent time before appreciable crystallization takes place, heat, operation, processing and cooled alloy.Therefore, for the non-crystaline amorphous metal with good formation ability, people expect that the crystallization curve promptly moves to the longer time to the right.The ability of non-crystaline amorphous metal opposing crystallization and alloy are relevant from the melt desired rate of cooling of formation amorphous that cools down.This is a unordered mutually stable sign during more than the glass transformation temperature non-crystaline amorphous metal being processed.We expect to suppress the crystalline rate of cooling is from per second 10
3K is to per second 1K or lower.When critical cooling rate reduces, before taking place, crystallization can obtain the longer processing treatment time, and promptly such non-crystaline amorphous metal can fully be heated to more than the glass transformation temperature and process under the situation that crystallization does not take place, and makes it be suitable for industrial use.
Amorphous alloy material provided by the invention can be used following formulate: Zr
a-[Nb (Ti)
1-xTa
x]
b-Cu
c-[Ni
1-yFe
y]
d-[Be
1-zAl
z]
e-Mg
f-Y
g, wherein a, b, c, d, e, f, g are atomic percent, and its variation range is: 25＜a＜66,1＜b＜15,8≤c≤20,1＜d＜20,5＜e＜40,0≤f≤36,0≤g＜5; X, y, z are atomic fraction, and its variation range is: 0≤x≤1,0＜y≤1,0≤z≤1.
Usually, the composition of non-crystaline amorphous metal contains transiting group metal elements and beryllium behind a preceding transiting group metal elements or one at least.The ternary alloy that contains beryllium has good amorphous formation ability usually.Yet the quad alloy that contains at least three transiting group metal elements has the critical cooling rate of the lower crystallization avoided, and therefore has better amorphous formation ability.However, the non-crystaline amorphous metal with better glass forming ability but finds in quinary alloy, particularly after containing at least two preceding transiting group metal elements and at least two in the alloy of transiting group metal elements.
Any transiting group metal elements of common 5% to 10% all is acceptable in non-crystaline amorphous metal.And non-crystaline amorphous metal allows to contain a spot of impurity, and for example a spot of oxygen may be dissolved in the non-crystaline amorphous metal and significant crystallization can not take place.The subsidiary element that also may contain other, for example germanium, phosphorus, carbon, nitrogen, but the total amount of impurity should be less than 5% (atomic percent).
The method that various expression alloying constituents are arranged, above-mentioned equation expression are wherein a kind of.In equation expression, generally express the shared ratio of various elements with algebraically, this ratio is complementary.Some occupies a high proportion of element of amorphous phase that can keep can overcome the tendency that other element promotes crystallization, as transiting group metal elements and beryllium.
The present invention also can add an amount of magnesium and yttrium.The content that its suitable composition is a magnesium is from 0～36% (unless stated otherwise, all referring to atomic percent here), and the composition of yttrium is from 0～5%, and its concrete selection depends on the content of other metallic element in the alloy.
Some occupies the performance that can influence non-crystaline amorphous metal than the element of small proportion, can increase the hardness of non-crystaline amorphous metal as iron.Yet the content of iron should be limited in 20% of alloy total amount, and suitable content is no more than 8%.In the alloy that contains zirconium, titanium, the content of the titanium in the alloy should be less than 15%.Non-crystaline amorphous metal of the present invention can contain and be up to 40% aluminium (atomic percent) or beryllium.
For realizing purpose of the present invention, material of the present invention need comprise the glassy phase or the amorphous phase of at least 50% volume percent.
Can use traditional method for preparing non-crystaline amorphous metal to obtain amorphous alloy material of the present invention.For example single roller gets rid of preparation band, paper tinsel and thin slices such as band or two rolling sheets.Specific implementation is as follows:
The present invention can adopt the zirconium rod through iodide decomposition purification of domestic production, prepares a series of zirconium base bulk-metallic glass that are suitable for domestic resources characteristic and are easy to the technology realization.
With 1～100K/s or lower rate of cooling cooling, the scantling of preparing is not less than 1 millimeter in each dimension with uniform alloy melt.Such rate of cooling can realize by multiple technologies: as the cold copper mold of alloy casting water inlet being obtained being of a size of 1～10 millimeter or bigger tabular, bar-shaped, strip or mesh members; Also can in quartz container, carry out cold quenching, obtain 30 millimeters or larger sized bar-shaped sample.
1) water quenching: purity is not less than 99.8% Zr, Nb, Ta, Cu, Ni, Fe, Be, Al, Mg, Y by required atom proportioning arc melting in the argon atmospher of titanium absorption, makes it to mix, cooling obtains mother alloy ingot.These ingot castings are packed into by pulverizing in the quartz glass tube, and vacuum is extracted into 10
-3Encapsulate behind the Pa, in stove, be heated to 1050 ℃ and keep making the ingot casting remelting in 10 minutes, shrend then, the Zr of acquisition uniform ingredients
a-[Nb
1-xTa
x]
b-Cu
c-[Ni
1-yFe
y]
d-[Be
1-zAl
z]
e-Mg
f-Y
gColumn bulk alloy, the alloy diameter can reach Φ=15mm.
2) teeming practice: purity is not less than 99.8% Zr, Nb, Ta, Cu, Ni, Fe, Be, Al, Mg, Y by needed atom proportioning arc melting in the argon atmospher of titanium absorption, makes it to mix, cooling obtains mother alloy ingot.With melting in high frequency furnace after the mother alloy ingot fragmentation, the vacuum tightness of high frequency furnace vacuum chamber is not less than 10 then
-1Pa, the fusing back is blown in the water cooled copper mould with argon gas.
3) vacuum suction casting technique: purity is not less than 99.8% Zr, Nb, Ta, Cu, Ni, Fe, Be, Al, Mg, Y by needed atom proportioning arc melting in the argon atmospher of titanium absorption, make it to mix, this electric arc furnace has absorbing and casting device, and alloy is injected copper mold.
The amorphous phase proportion can be estimated by differential thermal analysis, the heat content of release was compared when method was the heat content that discharges during with the heating of complete amorphous sample with partially-crystallized sample heating, its ratio can provide amorphous phase shared molar fraction in raw sample, can also determine the ratio of its amorphous phase in non-crystaline amorphous metal with tem study (TEM).The difference that non-crystalline material shows in the electron microscopic analysis method is very little, and the material of crystallization just has very big difference, and is easy to difference.Can differentiate phase with the method for transmission electron diffraction (TED) then.The volume fraction of the non-crystalline material in the sample also can be estimated with the transmission electron microscopy image.
Amorphous phase in the non-crystaline amorphous metal can verify by many currently known methodss.The X-ray diffractogram of non-crystaline amorphous metal has shown the scattering peak of a wide disperse fully.Fig. 3 to Fig. 5 is the X-ray diffraction analysis figure of non-crystaline amorphous metal of the present invention listed in the table 1, as seen from the figure, does not observe any crystallization peak in the effective resolution of X-ray diffractometer, illustrates that prepared alloy is a non-crystaline amorphous metal.In non-crystaline amorphous metal, contain the crystallization phase time, will observe the Bragg diffraction peak of sharp-pointed relatively representative crystallization phase.
Table 1 is the detail tabulation that can use the bar-shaped alloy of water quenching, teeming practice and vacuum suction casting technique acquisition, at least 1 millimeter of the diameter of these alloys or bigger, and be complete amorphous phase.The performance of these alloys is also listed in the table, comprises the glass transformation temperature (T with degree centigrade expression
g), crystallization temperature (T
x), fusing point (T
m), width (Δ T), hardness (HV) and the density (ρ) of supercooling liquid phase region, its temperature measurement technology is differential thermal analysis (DSC).Crystallization temperature is the heating rate of non-crystaline amorphous metal sample with 10 degrees centigrade of per minutes to be heated to more than the glass transformation temperature enthalpy change temperature indicative when crystallization of record begins.Owing to during sample measurement, in argon atmospher, carry out, and the commercial argon gas that uses comprises some oxygen usually, thus sample after adding thermal measurement, the surface has some oxidations.When the sample surface was cleaned very much so that homogeneous nucleation rather than heterogeneous nucleation take place, crystallization temperature can be higher.Therefore the temperature height that obtains than the oxidized back of sample surfaces in these trials of the crystallization temperature of actual sample.The supercooling liquid phase region width is the poor of the crystallization temperature that obtains in differential thermal analysis is measured and glass transformation temperature.Usually, the supercooling liquid phase region of broad shows that non-crystaline amorphous metal has lower critical cooling rate.Be that non-crystaline amorphous metal has the longer treatment time more than glass transformation temperature.
Non-crystaline amorphous metal provided by the invention has high rigidity, and its value major part is approaching or surpass 6Gpa, and high Vicker hardness has indicated high strength.Can see that from table 1 crystallization temperature of most of alloy surpasses 700K, glass transformation temperature surpasses 650K, and this illustrates that they have better thermostability.Non-crystaline amorphous metal provided by the invention is not having crystalline situation lower critical rate of cooling all at 1～100K/s, and has quite wide supercooling liquid phase region, shows that they all have good amorphous formation ability.With three kinds of preparation methods of the present invention, can both obtain the non-crystalline material of millimeter magnitude, overall dimension can reach 20 millimeters.
The present invention will be further described below in conjunction with drawings and Examples:
Fig. 1 is the heat content of typical non-crystaline amorphous metal and the curve of temperature,
Fig. 2 is non-crystaline amorphous metal logarithm synoptic diagram as the temperature and the viscosity of supercooled liquid between fusing point and glass transformation temperature,
Fig. 3～Fig. 5 is the X-ray diffractogram of non-crystaline amorphous metal of the present invention,
Fig. 6 is heat analysis (DTA) curve of several non-crystaline amorphous metals of the present invention,
Fig. 7 is heat analysis (DSC) curve of the non-crystaline amorphous metal of embodiments of the invention 1,
Fig. 8 is the sample photo of (C) after (B) before the ultrasonic measurement (A), thermal distortion of Zr/Nb base noncrystal alloy, the thermal distortion.
Embodiment 1:
With purity be 99.9% to 99.999% Zr, Ti, Cu, Ni, Be and Fe by needed atom proportioning arc melting in the argon atmospher of titanium absorption, make it to mix, cooling obtains ingot casting.These ingot castings are packed into by pulverizing in the quartz glass tube, pumping high vacuum (10
-3Pa) back encapsulation makes the ingot casting remelting in stove, shrend then, the Zr of acquisition uniform ingredients
48Nb
8Cu
14Ni
12Be
18Column bulk alloy, diameter are 8 millimeters, if can obtain larger sized non-crystaline amorphous metal with die cast.X ray and transmission electron microscope turn out to be complete amorphous.Can record its glass transformation temperature (T from the DSC curve
g), initial crystallization temperature (T
x) and the peak temperature (T at each crystallization peak
Pi).The characteristics of this alloy are to have higher fusing point T
m(997K) with crystallization temperature T
x(724K), so thermostability is better, higher (the relative Zr of the temperature that is suitable for
41Ti
14Cu
12.5Ni
10Be
22.5), its glass transformation temperature is 656K.The supercooling liquid phase region width of this alloy is 68K, illustrates that its amorphous formation ability is fine.Density is 6.70g/cm
3, hardness is 6.09GPa, has surpassed Zr
41Ti
14Cu
12.5Ni
10Be
22.5, this indicates that it has higher intensity.Its Young's modulus is 93.7GPa in addition.
Embodiment 2:
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing is [Zr
55Cu
20Ni
10Al
15]
96Y
4This alloy is at Zr
55Cu
20Ni
10Al
15In the alloy, add that a spot of rare earth element yttrium obtains.The adding of a spot of rare earth element yttrium has reduced zirconium-base amorphous susceptibility to oxygen, has improved the amorphous formation ability of alloy, makes alloy have higher and better manufacturability.The characteristics of this alloy are to have higher fusing point T
m(1012K) with crystallization temperature T
x(756K), its glass transformation temperature is 684K, and its supercooling liquid phase region width is 72K, illustrates that its thermostability and amorphous formation ability are better than the bulk amorphous alloys of embodiment 1 preparation.The density of this alloy is 6.44g/cm
3, hardness is 5.93GPa, compares Zr
41Ti
14Cu
12.5Ni
10Be
22.5(hardness is 5.4GPa) is high slightly.Its Young's modulus is 86GPa in addition.
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing are Zr
48Nb
8Cu
12Fe
8Be
24, this alloy is to obtain with the Ni in the Fe alternative embodiment 1.Can make the pole of 8 mm dias with embodiment 1 described technical scheme.This alloy has been owing to replaced comparatively expensive metallic nickel with comparatively cheap iron, thus reduced cost, and also this alloy has the Zr of being better than
48Nb
8Cu
14Ni
12Be
18Thermostability.This alloy can carry out superplastic deformation in 410 ℃ air, distortion back alloy still is a non-crystal structure, and is therefore highly beneficial to the moulding of material.The fusing point T of this alloy
mBe 1009K, crystallization temperature T
xBe 751K, glass transformation temperature is 658K.The supercooling liquid phase region width of this alloy can reach 93K, illustrates that its amorphous formation ability is better than the alloy of embodiment 1 and embodiment 2.The density of this alloy is 6.44g/cm
3, hardness is 5.85GPa, Young's modulus is 95.7GPa.
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing are Zr
26Ti
10Mg
24Be
20Cu
8Ni
8Y
4, this alloy is to contain minimum a kind of of zirconium in the various alloy provided by the present invention, and contains magnesium and rare earth element yttrium.The interpolation rare earth element of trace is to the zirconium-base amorphous promoter action that is formed with, and rare earth element has very high chemically reactive, and its existence can change the structure of impurity in the alloy, reduces the oxygen level in the alloy.Magnesium and beryllium are same main group elements, but magnesium is nontoxic.So replacing beryllium with magnesium is a kind of good selection.Magnesium is the highest can be increased to 36% (atomic percent), and the amorphous formation ability of alloy does not change.The glass transformation temperature of this alloy is 650K, and crystallization temperature is 700K, and fusing point is 894K, and the supercooling liquid phase region width is 50K.
Embodiment 5
Purity is not less than 99.98% zr, Cu, Ni, Al by needed atom proportioning arc melting in the argon atmospher of titanium absorption, makes it to mix, cooling obtains mother alloy ingot.With melting in high frequency furnace after the mother alloy ingot fragmentation, the vacuum tightness of high frequency furnace vacuum chamber is not less than 10 then
-1Pa, the fusing back is blown in the water cooled copper mould with argon gas, and the composition of the bulk amorphous alloys of preparing is Zr
65Al
7.5Cu
17.5Ni
10The glass transformation temperature of this alloy is 651K, and crystallization temperature is 736K, and fusing point is 1038K, and its supercooling liquid phase region width can reach 85K.Because the crystallization temperature of this alloy is higher, so its thermostability is fine.This alloy needs high pure metal material and high vacuum in the preparation.
Embodiment 6
Technical scheme such as embodiment 5, the composition of the bulk amorphous alloys of preparing are Zr
52.5Ti
2.5Cu
20Ni
10Al
15The glass transformation temperature of this alloy is 638K, and crystallization temperature is 708K, and fusing point is 1098K, and the width of supercooling liquid phase region is 70K.This alloy has the fusing point higher than embodiment 5, and still, crystallization temperature is than embodiment 5 low 28K.This hardness of alloy is 5.20Gpa, and density is 6.49g/cm
3The tensile break strength of this alloy is 1800Mpa, illustrates that it has better mechanical property.
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing are Zr
34Ti
15Cu
10Ni
11Be
28Y
2This alloy has added a spot of rare earth element yttrium, has reduced zirconium-base amorphous susceptibility to oxygen, has improved the amorphous formation ability of alloy, makes alloy have higher and better manufacturability.The glass transformation temperature of this alloy is 650K, and crystallization temperature is 695K, and fusing point is 910K, and the supercooling liquid phase region width is 45K.Its density is 5.78g/cm
3, be lower a kind of in various non-crystaline amorphous metals provided by the invention, and its hardness is 6.07Gpa, it has higher intensity higher hardness indication, so it has higher strength to density ratio.
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing are Zr
36Nb
12Mg
12Be
20Cu
10Ni
6Y
2Fe
2This alloy is to contain maximum one of constituent element in the non-crystaline amorphous metal provided by the invention, and its glass transformation temperature is 678K, and crystallization temperature is 735K, and fusing point is 983K, and supercooled liquid is 57K to sector width.
Embodiment 9
Technical scheme such as embodiment 1, the composition of the bulk amorphous alloys of preparing are Zr
26Ti
9Cu
8Ni
6Be
15Mg
36The glass transformation temperature of this alloy is 608K, and crystallization temperature is 704K, and fusing point is 955K.This alloy is the wideest a kind of of supercooling liquid phase region in the non-crystaline amorphous metal provided by the invention, and this illustrates that it has extraordinary amorphous formation ability.
Table 1
| Composition | T g，K | T x，K | T m，K | ΔT，K | HV， GPa | ρ， g/cm 3 |
| Zr 48Nb 8Cu 12Fe 8Be 24 | 658 | 751 | 1009 | 93 | 5.85 | 6.44 |
| Zr 48Nb 8Cu 14Ni 12Be 18 | 656 | 724 | 997 | 68 | 6.09 | 6.70 |
| [Zr 55Cu 20Ni 10Al 15] 96Y 4 | 663 | 740 | 1067 | 77 | 5.93 | 6.44 |
| [Zr 55Cu 20Ni 10Al 15] 98Y 2 | 714 | 787 | 1057 | 73 | 6.49 | 6.56 |
| Zr 40Ti 15Cu 11Ni 11Be 21.5Y 1Mg 0.5 | 625 | 674 | 905 | 49 | 5.74 | 6.05 |
| Zr 34Ti 15Cu 10Ni 11Be 28Y 2 | 650 | 695 | 910 | 45 | 6.07 | 5.78 |
| Zr 36Nb 12Mg 12Be 20Cu 10Ni 6Y 2Fe 2 | 678 | 735 | 983 | 57 | ||
| Zr 36Nb 12Mg 12Be 20Cu 10Ni 8Y 2 | 644 | 712 | 993 | 68 | ||
| Zr 26Ti 10Mg 24Be 20Cu 8Ni 8Y 4 | 650 | 700 | 894 | 50 | ||
| Zr 65Al 7.5Ni 10Cu 17.5 | 651 | 736 | 1038 | 85 | 6.77 | |
| Zr 52.5Ti 2.5Cu 20Ni 10Al 15 | 638 | 708 | 1098 | 70 | 5.20 | 6.49 |
| [Zr 41Ti 14Cu 12.5Ni 10Be 22.5] 98Y 2 | 675 | 725 | 930 | 50 | 6.76 | |
| Zr 45Nb 10Cu 13Ni 10Be 22 | 670 | 740 | 990 | 70 | 6.32 | 6.52 |
| Zr 45Nb 8Cu 13Ni 4Be 22Fe 8 | 665 | 725 | 985 | 60 | 6.08 | 6.54 |
| Zr 26Ti 9Cu 8Ni 6Be 15Mg 36 | 608 | 704 | 955 | 96 |
Claims (4)
1. block non-crystalline alloy material is characterized in that: use following formulate: Zr
a-[Nb (Ti)
1-xTa
x]
b-Cu
c-[Ni
1-yFe
y]
d-[Be
1-zAl
z]
e-Mg
f-Y
g, wherein a, b, c, d, e, f, g are atomic percent, and its variation range is: 25＜a＜66,1＜b＜15,8≤c≤20,1＜d＜20,5＜e＜40,0≤f≤36,0≤g＜5; X, y, z are atomic fraction, and its variation range is: 0≤x≤1,0≤y≤1,0≤z≤1.
2. by the described block non-crystalline alloy material of claim 1, it is characterized in that: any transiting group metal elements that also can contain 5% to 10% atomic percent.
3. by the described block non-crystalline alloy material of claim 1, it is characterized in that: also can contain total amount and be less than 5% atomic percent impurity.
4. by the described block non-crystalline alloy material of claim 1, it is characterized in that: the amorphous phase that need comprise at least 50% volume percent.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB01118261XA CN1137282C (en) | 2001-05-25 | 2001-05-25 | Massive amorphous alloy material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB01118261XA CN1137282C (en) | 2001-05-25 | 2001-05-25 | Massive amorphous alloy material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1388264A true CN1388264A (en) | 2003-01-01 |
| CN1137282C CN1137282C (en) | 2004-02-04 |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100348878C (en) * | 2004-11-16 | 2007-11-14 | 燕山大学 | Bulk amorphous alloy rotary bearing and production thereof |
| CN100582529C (en) * | 2003-09-02 | 2010-01-20 | 并木精密宝石株式会社 | Precision gear, and production method of precision gear |
| WO2011050680A1 (en) * | 2009-10-26 | 2011-05-05 | Byd Company Limited | Zr-BASED AMORPHOUS ALLOY AND PREPARING METHOD THEREOF |
| CN102534439A (en) * | 2012-02-12 | 2012-07-04 | 北京航空航天大学 | Nickel-free low-copper zirconium-based bulk amorphous alloy and preparation method thereof |
| CN104264081A (en) * | 2014-09-22 | 2015-01-07 | 北京理工大学 | Endogenous-phase titanium-based amorphous composite material with improved strength and plasticity and preparation method thereof |
| CN110106456A (en) * | 2018-01-19 | 2019-08-09 | 东莞市坚野材料科技有限公司 | A kind of amorphous alloy bracket and preparation method thereof |
| CN115354246A (en) * | 2022-08-24 | 2022-11-18 | 盘星新型合金材料(常州)有限公司 | Rare earth modified light block amorphous alloy and preparation method and application thereof |
-
2001
- 2001-05-25 CN CNB01118261XA patent/CN1137282C/en not_active Expired - Fee Related
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100582529C (en) * | 2003-09-02 | 2010-01-20 | 并木精密宝石株式会社 | Precision gear, and production method of precision gear |
| CN101709773B (en) * | 2003-09-02 | 2012-07-18 | 并木精密宝石株式会社 | Precision gear and production method of precision gear |
| CN100348878C (en) * | 2004-11-16 | 2007-11-14 | 燕山大学 | Bulk amorphous alloy rotary bearing and production thereof |
| WO2011050680A1 (en) * | 2009-10-26 | 2011-05-05 | Byd Company Limited | Zr-BASED AMORPHOUS ALLOY AND PREPARING METHOD THEREOF |
| CN102534439A (en) * | 2012-02-12 | 2012-07-04 | 北京航空航天大学 | Nickel-free low-copper zirconium-based bulk amorphous alloy and preparation method thereof |
| CN104264081A (en) * | 2014-09-22 | 2015-01-07 | 北京理工大学 | Endogenous-phase titanium-based amorphous composite material with improved strength and plasticity and preparation method thereof |
| CN110106456A (en) * | 2018-01-19 | 2019-08-09 | 东莞市坚野材料科技有限公司 | A kind of amorphous alloy bracket and preparation method thereof |
| CN110106456B (en) * | 2018-01-19 | 2021-12-17 | 东莞市坚野材料科技有限公司 | Amorphous alloy stent and preparation method thereof |
| CN115354246A (en) * | 2022-08-24 | 2022-11-18 | 盘星新型合金材料(常州)有限公司 | Rare earth modified light block amorphous alloy and preparation method and application thereof |
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| CN1137282C (en) | 2004-02-04 |
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