CN106282663B - A kind of Zr based superelastic alloys and preparation method thereof - Google Patents
A kind of Zr based superelastic alloys and preparation method thereof Download PDFInfo
- Publication number
- CN106282663B CN106282663B CN201510317131.7A CN201510317131A CN106282663B CN 106282663 B CN106282663 B CN 106282663B CN 201510317131 A CN201510317131 A CN 201510317131A CN 106282663 B CN106282663 B CN 106282663B
- Authority
- CN
- China
- Prior art keywords
- alloy
- superelastic alloys
- based superelastic
- preparation
- vacuum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Landscapes
- Materials For Medical Uses (AREA)
- Dental Prosthetics (AREA)
Abstract
The invention discloses a kind of Zr based superelastic alloys and preparation method thereof, belong to technical field of metal material.The alloy composition is ZraCubNbcCodAleREf, wherein：A=45~55, b=39~50, c=1~10, d=0~5, e=0~4, f=0~2, a+b+c+d+e+f=100.The alloy has Thermoelastic Martensitic Transformation in A characteristic, and maximum shape memory effect 2.1%, maximum room temperature super-elasticity 4.2%, has good plasticity concurrently.Compared with NiTi series superelastic alloy, the Zr based superelastic alloys, have lower fusing point, are more suitable for the Die Casting technique of complex component, and production method is simple；Without toxic element, such as Ni, Cr, V, there is more preferable biocompatibility.It is with a wide range of applications in fields such as bio-medical, communications and transportation, consumer electronics, aerospaces.
Description
Technical field
The invention belongs to technical field of metal material, and in particular to a kind of Zr based superelastic alloys and preparation method thereof.
Background technology
Superelastic alloy because with it is higher reply phase transformation pseudoelastic strain be widely used in aerospace, accurate instrument
The fields such as device, bio-medical.The superelastic alloy being most widely used at present is NiTi bianry alloys.But NiTi bianry alloys
There are shortcomings, such as superlastic sexual behaviour to belong to the superlastic sexual behaviour of wide transformation hysteresis, and in-fighting is high；The Ni ions of its dissolution have cell
Toxicity, easily causes human allergy to react；Alloy melting point is high, complex production process etc..Therefore, Development of Novel superior performance is super
Elastic alloy has become the hot issue of current research.
Deng atomic ratio ZrCu alloys also have similar to NiTi bianry alloys transformation behavior, but its strain response rate compared with
Difference, limits its application.Such as document 1 (Koval YuN, Firstov GS, Van Humbeeck J, Delaey L, Jang
WY.J Phys IV C81995；5:1103-8.) the atomic ratio ZrCu alloys such as report only can be real less than 0.4% strain in application
Now recover completely, after 0.4% strain, strain response rate drops to less than 90%；Document 2 (Firstov G, Van
Humbeeck J,Koval YN.Scripta Mater.2004；50:243-8.) report and surpass in ZrCuCoNiTi Alloy At Room Temperatures
Elasticity about 1.4%, but strain response rate and be less than 50%.Therefore, Zr base of the exploitation with high super-elasticity and Large strain response rate
Alloy is of great significance for its application.
The content of the invention
For the shortcomings of the prior art, it is an object of the invention to provide a kind of Zr based superelastic alloys and
Its preparation method, by adding cobalt, niobium, aluminium and rare earth in zirconium acid bronze alloy, can effectively modulate thermo elastic martensite and turn
Change behavior, improves the shape-memory properties of alloy, obtains larger phase transformation super-elasticity.
To achieve the above object, the technical solution used in the present invention is：
A kind of Zr based superelastic alloys, by atomic percentage, the chemical composition of the alloy is：
ZraCubNbcCodAleREf, wherein：A=45~55, b=39~50, c=1~10, d=0~5, e=0~4, f=0~2, a+
B+c+d+e+f=100；RE is the one or more in rare earth element (including Y element).
The chemical composition of the Zr based superelastic alloys is preferably (pressing atomic percentage)：ZraCubNbcCodAleREf,
Wherein：A=46~50, b=39~49, c=1~10, d=0~2, e=0~4, f=0~1, a+b+c+d+e+f=100；RE
For the one or more in rare earth element (including Y element).
In the chemical composition of the Zr based superelastic alloys, Co constituent contents are more preferably 1~2at.%, Al constituent contents
More preferably 1~4at.%.
The above-mentioned Zr based superelastic alloys of the present invention are prepared as follows：
(1) using the metal of technical grade purity as raw material, each component is weighed into mixing according to composition proportion and obtains metal
Mixture；
(2) in an inert atmosphere, gained metal mixture is made by alloy using electric arc or induction melting method, melted repeatedly
Refining is uniform to component, obtains master alloy ingot；Wherein：Foundry alloy smelting parameter is：Melting 200~700A of electric current, vacuum 10-2~
10-4Pa；
(3) master alloy ingot of preparation is melted by electric arc or sensing heating, using copper mold casting method, vacuum water quenching method or
The alloy bar material of size and dimension needed for vacuum die-casting method acquisition；Wherein：Alloy bar material preparation technology parameter is：Vacuum 100
~10-4Pa, cooling velocity 1~102K/s, alloy melt temperature are more than alloy melting point 50~400 DEG C；
(4) using being machined, the alloy bar material that step (3) obtains is made to the alloy sample of required shape.
Advantages of the present invention：
1st, the present invention is introducing Co, Nb, Al and RE conjunction on the basis of atomic ratio ZrCu alloys (Zr50Cu50, at.%) are waited
Gold element, so that the Zr based superelastic alloys with good superelastic properties and shape memory effect be made.The present invention is logical
The addition of alloy element is crossed, has modulated the Thermoelastic Martensitic Transformation in A behavior of alloy, Zr based superelastic alloys is breached and faces
The problem of " strain response rate is low ", realize maximum shape memory effect 2.1%；There is superlastic sexual behaviour at room temperature, it is maximum
For 4.2%；Apply 4~5% strain when, strain response rate up to more than 98% (including shape memory effect and super-elasticity) very
Replied to complete.
2nd, Zr based superelastic alloys of the present invention, repeat to load in same stress, can obtain with narrow hysteresis superlastic sexual behaviour,
Response rate is strained up to more than 98%.
3rd, Zr based superelastic alloys of the present invention are free of bio-toxicity element, and such as Ni, Cr, V, have more preferable than TiNi alloy
Biocompatibility, there is important application prospect in bio-medical field.
4th, Zr based superelastic alloys of the present invention prepare and use technical grade raw material, and the cost of raw material is cheap；The Zr bases surpass
The fusing point of elastic alloy has lower fusing point compared with TiNi alloy, is more suitable for complex-shaped between 850~950 DEG C
The die casting precise forming process of component, is abbreviated system, technique is simple, and expense is low；In communications and transportation, consumer electronics and aviation
The fields such as space flight have great application prospect.
Brief description of the drawings
Fig. 1 is Zr46Cu45Nb3Co2Al4The compression curve of alloy.
Fig. 2 is Zr46Cu45Nb3Co2Al4The compression-loaded unloading curve of alloy.
Fig. 3 is Zr46Cu45Nb3Co2Al4The cyclic compressive load unloading curve of alloy.
Fig. 4 is Zr46Cu45Nb3Co2Al4The compression-loaded unloading front-end geometry of alloy develops X ray diffracting spectrum.
Fig. 5 is Zr46Cu43Nb5Co2Al4The super-elasticity of the different cyclic compressive load uninstall process of alloy and strain can return
Multiple rate.
Fig. 6 is Zr46Cu43Nb5Co2Al4The high temperature DSC curve of alloy.
Fig. 7 is Zr46Cu49Nb3Co2Martensite changes DSC curve to austenite in alloy heating process.
Embodiment
The present invention is described in further detail with reference to the accompanying drawings and examples.
Zr based superelastic alloys composition of the present invention is ZraCubNbcCodAleREf(pressing atomic percentage), wherein：A=45
~55, b=39~50, c=0~10, d=0~5, e=0~4, f=0~2, a+b+c+d+e+f=100；Preferably：A=46
~50, b=39~49, c=0~10, d=0~2, e=0~4, f=0~1, a+b+c+d+e+f=100；RE is rare earth element
One or more in (including Y).Alloying component such as table 1 in each embodiment.
1 embodiment alloying component (atomic percent) of table
| Sequence number | Zr | Cu | Nb | Co | Al | RE | It is total |
| Embodiment 1 | 46 | 49 | 3 | 2 | 0 | 0 | 100 |
| Embodiment 2 | 46 | 47 | 3 | 2 | 2 | 0 | 100 |
| Embodiment 3 | 46 | 45 | 3 | 2 | 4 | 0 | 100 |
| Embodiment 4 | 46 | 43 | 5 | 2 | 4 | 0 | 100 |
| Embodiment 5 | 46 | 41 | 7 | 2 | 4 | 0 | 100 |
| Embodiment 6 | 46 | 39 | 9 | 2 | 4 | 0 | 100 |
| Embodiment 7 | 48 | 43 | 3 | 2 | 4 | 0 | 100 |
| Embodiment 8 | 50 | 41 | 3 | 2 | 4 | 0 | 100 |
| Embodiment 9 | 55 | 36 | 2 | 3 | 4 | 0 | 100 |
| Embodiment 10 | 49 | 41 | 3 | 2 | 4 | Y 1 | 100 |
| Embodiment 11 | 49.5 | 41 | 3 | 2 | 4 | Gd 0.5 | 100 |
| Embodiment 12 | 46 | 45 | 5 | 0 | 4 | 0 | 100 |
| Embodiment 13 | 46 | 43 | 3 | 2 | 4 | Y 1+La 1 | 100 |
Zr based superelastic alloys are prepared according to the following steps in following embodiments：
The first step, component using the metal of technical grade purity as raw material, weighed according to composition proportion and mixed；
Second step, in an inert atmosphere, utilizes electric arc or induction melting method melting thing mixed above.Utilize arc method
During melting, first vacuum chamber is evacuated to and is made 10-2~10-4Pa, is then charged with high-purity argon gas, until vacuum meter shows 8 × 104~
4×104Pa.Alloy melting electric current is 200~700A, and each smelting time 2~30 minutes, after each melting, overturns alloy,
Melting again, is at least repeated four times, until alloying component is uniform.During using induction melting, using CaO or Al2O3Crucible, first will
Vacuum chamber is evacuated to 10-2~10-4Pa, is then charged with high-purity argon gas, until vacuum meter shows 8 × 104~4 × 104Pa, gradually adds
It is high-power alloy melting temp is higher than 50~150 DEG C of alloy melting point to 30kW, stir, treat that alloy is completely melt, uniformly, fall
Enter in metal pattern, obtain master alloy ingot.
3rd step, different sizes, shape alloy material are obtained using copper mold casting method, vacuum water quenching method or vacuum die-casting method
Material.Using mechanical processing, be made needed for shape sample.Sample preparation technological parameter is：Vacuum 100~10-4Pa, cooling speed
Degree 1~102K/s, alloy melt temperature are more than alloy melting point 50~400 DEG C.
The characterization of alloy property and sampling：Sawed using low speed cutting, on Zr based superelastic alloys material obtained above,
It is 1 × 1 × 0.5mm to cut size3Block as phase transformation test sample, using NETZSCH404C types means of differential scanning calorimetry point
It is 20 DEG C/min that analyzer, which measures martensitic transformation temperature and fusion temperature, the rate of heat addition,；Using the method for wire cutting, major diameter is cut
Than being that 1.5 (such as diameter 6mm, length 9mm or diameter 4mm, length 6mm) samples are used as compression sample, Instron 4401 is used
Type universal testing machine carries out room temperature compression experiment, compression speed 0.27mm/min.Shape memory effect measures：First plus
Different prestrain is downloaded to, is then unloaded, is being heated to more than phase transition temperature, recovery of shape is measured after being cooled to room temperature, takes it
In maximum be shape memory effect；Super-elasticity measures：Method one, is first loaded into different predeformation amounts, and rear unloading, leads to
Recovery strain after curved measurement unloads is crossed, obtains super-elasticity.Method two, under a certain stress, starts, CYCLIC LOADING, unloading, together
Shi Jilu load-deformation curves, recovery strain is obtained by measuring.
Embodiment 1：
The present embodiment Zr46Cu45Nb3Co2Al4Alloy preparation method is as described below：
The first step：Matched according to alloying component, weigh metal Zr, Cu, Nb, Co and Al of each technical grade purity；
Second step：Each raw material metal that will have been weighed, is put into non-consumable arc furnace crucible, and wherein Zr and Nb first melt
Refining, then adds the melting together of other constituent elements.During melting, vacuum cavity is first evacuated to 2 × 10-3Pa, is then charged with high-purity argon
Gas, 8 × 10 are shown to vacuum meter4Pa.Alloy melting electric current is 200~700A, each smelting time 5 minutes, each melting it
Afterwards, alloy is overturn, melting again, repeats five times, and obtains master alloy ingot.
3rd step：Diameter 10mm, length 80mm and diameter 5mm are prepared using copper mold casting method, length is 80mm alloy bars
Material.First master alloy ingot is put into water jacketed copper crucible, vacuum chamber is evacuated to 2 × 10-3Pa, is then charged with high-purity argon gas, to true
Empty table shows 8 × 104Pa.1200 DEG C of melted alloys 1 minute, then aluminium alloy is poured into the copper mold of corresponding size, closed
Golden bar.
Using the method for wire cutting, diameter 6mm, length 9mm samples are cut from diameter 10mm, length 80mm alloy bar materials
Product, cut diameter 4mm, length 6mm samples from diameter 5mm, length 80mm alloy bar materials.Room temperature compression experiment uses
5582 type universal testing machines of Instron carry out, compression speed 0.27mm/min.The pressure of diameter 6mm, length 9mm samples
Contracting curve is as shown in Figure 1.Yield strength (the σ of alloy material0.2) it is about 760MPa, strong processing hardening is shown after surrender
Phenomenon, total deformation are about 6.5%, and fracture strength is up to 1600~1650MPa, and Young's modulus is about 49.7GPa through measurement.Add
Unloaded after being loaded onto 1300MPa, curve is as shown in Figure 2.Alloy shows superlastic sexual behaviour, and about 2.8%.After unloading, by alloy
Sample is heated to 200 DEG C, and water quenching, it is found that alloy has shape memory effect, and about 1.7%.To sum up, apply when to alloy
During 4.5% deformation, unloading and heating can make alloy sample find that strain is replied completely.CYCLIC LOADING curve is as shown in figure 3, by scheming
As can be seen that after second circulation, superelastic strain is 2.1%~2.5%, and unloading strain is replied more than 98%, if into
One step increases CYCLIC LOADING number, can further improve unloading strain response rate.In addition, alloy material can also be seen that by Fig. 3
Show narrow hysteresis superlastic sexual behaviour.Front and rear structural evolution X ray diffracting spectrum is unloaded by the compression-loaded of comparative alloy,
As shown in Figure 4, it is found that the superlastic sexual behaviour of alloy can be attributed to the generation of martensitic traoformation.Diameter 4mm, length 6mm
The compression experiment of sample shows, is unloaded after 1500MPa is loaded onto, and alloy shows superlastic sexual behaviour, about 4.2%.
Sawed using low speed cutting, on obtained Zr based superelastic alloys material, it is 1 × 1 × 0.5mm to cut size3's
Block is as heat analysis sample.Fig. 5 gives corresponding high temperature DSC curve.As seen from the figure, the solidus temperature of alloy (starts
Fusion temperature) it is about 877 DEG C, liquidus temperature is about 960 DEG C, far below NiTi bianry alloys.
Embodiment 2：
Difference from Example 1 is：Alloying component is different, and alloy melting method is different.
Alloying component is Zr in the present embodiment46Cu43Nb5Co2Al4, alloy melting method uses vacuum induction melting.Vacuum
During induction melting, using Al2O3Crucible, raw material are sequentially sequentially placed into crucible from high to low according to fusing point.First by vacuum chamber
It is evacuated to and is made 1 × 10-2Pa, is then charged with high-purity argon gas, until vacuum meter shows 5 × 104Pa, is gradually increased power to 30kW,
Alloy melting temp is higher than 100~150 DEG C of alloy melting point, stir, treat that alloy is completely melt, uniformly, pour into metal pattern, obtain
Obtain master alloy ingot.
Diameter 6mm, the compression test of length 9mm samples show Zr46Cu43Nb5Co2Al4Alloy yield strength (σ0.2) about
720MPa, shows strong processing hardening phenomenon after surrender, total deformation is about 6%, and fracture strength is up to about 1600MPa,
Young's modulus is about 59.6GPa through measurement.Loading stress is 1300MPa, recovery strain and strain in CYCLIC LOADING uninstall process
Response rate is as shown in fig. 6, maximum super-elasticity is 3.6%, and during the tenth circulation, superelastic strain 2.8%, unloading strain is replied
More than 98%, for narrow hysteresis superlastic sexual behaviour.1300MPa samples will be pre-loaded to and be heated to 300 DEG C, after water quenching, Ke Yifa
Existing alloy has shape memory effect, and about 0.8%.DSC tests the solidus temperature (beginning fusion temperature) for showing the alloy
About 875 DEG C, liquidus temperature is about 960 DEG C.
Embodiment 3：
Difference from Example 1 is：Alloying component is Zr in the present embodiment46Cu41Nb7Co2Al4。
Diameter 6mm, the compression test of length 9mm samples show Zr46Cu41Nb7Co2Al4Alloy yield strength (σ0.2) about
610MPa, shows strong processing hardening phenomenon after surrender, total deformation is about 8.1%, and fracture strength is up to about
1760MPa.The super-elasticity of alloy is 1.7%~2.3%.DSC experiments show that the solidus temperature of the alloy (starts fusing temperature
Degree) it is about 875 DEG C, liquidus temperature is about 960 DEG C.
Embodiment 4：
Difference from Example 1 is：Alloying component is Zr46Cu49Nb3Co2 in the present embodiment.
Diameter 6mm, the compression test of length 9mm samples show that the Alloy At Room Temperature fracture strength is up to about 1700MPa, total to become
Shape amount is about 4.7%, and maximum super-elasticity is up to 4%.DSC experiments show the solidus temperature (beginning fusion temperature) of the alloy about
For 900 DEG C, liquidus temperature is about 1000 DEG C.In heating process, martensite changes to austenite in alloy, as shown in fig. 7, opening
Beginning temperature is about 142 DEG C, and end temp is about 182 DEG C.
Embodiment 5：
Difference from Example 1 is：Alloying component is Zr in the present embodiment46Cu39Nb9Co2Al4。
Diameter 6mm, the compression test of length 9mm samples show the Alloy At Room Temperature fracture strength about 1430MPa, total deformation
About 3.8%, maximum super-elasticity is up to 2%.DSC experiments show the solidus temperature (beginning fusion temperature) of the alloy about
875 DEG C, liquidus temperature is about 960 DEG C.
Embodiment 6：
Difference from Example 1 is：Alloying component is Zr in the present embodiment46Cu47Nb3Co2Al2。
Yield strength (the σ of diameter 6mm, length 9mm samples0.2) it is about 670MPa, it is hard that strong processing is shown after surrender
Change phenomenon, total deformation is about 5.6%, fracture strength about 1450MPa, and Young's modulus is about 37.6GPa through measurement.It is loaded onto
Being unloaded after 1300MPa, alloy shows superlastic sexual behaviour, and about 3%.During CYCLIC LOADING, it is super that alloy material shows narrow hysteresis
Elastic behavior.
DSC experiments show that the solidus temperature (beginning fusion temperature) of the alloy is about 870 DEG C, and liquidus temperature is about
970℃。
Embodiment 7-10：
Difference from Example 1 is：The alloying component of embodiment 7-10 is followed successively by Zr48Cu43Nb3Co2Al4,
Zr50Cu41Nb3Co2Al4, Zr55Cu36Nb3Co2Al4, Zr46Cu45Nb5Al4。
Diameter 6mm, the compression test of length 9mm samples show the yield strength (σ of above alloy material0.2) be about 500~
700MPa, shows strong processing hardening phenomenon after surrender, total deformation is about 5~10%, and fracture strength about 1400~
1800MPa.Above alloy shows superlastic sexual behaviour, and about 1.8~4%.During CYCLIC LOADING, alloy material shows narrow hysteresis
Superlastic sexual behaviour.
DSC experiments show that the solidus temperature (beginning fusion temperature) of above alloy is about 850~880 DEG C, liquidus curve temperature
About 950~1050 DEG C of degree.
Embodiment 11：
The present embodiment alloying component is Zr49Cu41Nb3Co2Al4Y1Alloy, preparation method are as described below：
The first step：Matched according to alloying component, weigh metal Zr, Cu, Nb, Co of each technical grade purity, Al and Y；
Second step：Each raw material metal that will have been weighed, is put into non-consumable arc furnace crucible, in three batches secondary melting, first
The melting of Zr and Nb elder generations, then ZrNb intermediate alloy ingots melting together with Cu, Co, Al constituent element, last ZrNbCuCoAl alloy pigs and Y
Melting.During melting, vacuum cavity is first evacuated to 8 × 10-3Pa, is then charged with high-purity argon gas, and 8 × 10 are shown to vacuum meter4Pa.Close
Golden melting electric current is 200~700A, and each smelting time 5 minutes, after each melting, overturns alloy, melting again, repeats five
It is secondary, obtain master alloy ingot.
3rd step：Diameter 10mm, length 80mm bars are prepared using copper mold casting method.Master alloy ingot is first put into water-cooled copper
In crucible, vacuum chamber is evacuated to 20Pa, is then charged with high-purity argon gas, 8 × 10 are shown to vacuum meter4Pa.1200 DEG C of fusings are closed
Gold 1 minute, then pours into aluminium alloy in copper mold, obtains alloy bar material.
Yield strength (the σ of diameter 6mm, length 9mm samples0.2) it is about 750MPa, it is hard that strong processing is shown after surrender
Change phenomenon, total deformation is about 6%, fracture strength about 1750MPa.Alloy shows superlastic sexual behaviour, and about 2~3%.Unloading
Afterwards, alloy sample being heated to 200 DEG C, water quenching, it is found that alloy has shape memory effect, about 1.7%.
DSC experiments show that the solidus temperature (beginning fusion temperature) of the alloy is about 865 DEG C, and liquidus temperature is about
950℃。
Embodiment 12~13：
It is with 11 difference of embodiment：Alloying component in embodiment 12 and 13 is respectively
Zr49.5Cu41Nb3Co2Al4Gd0.5And Zr46Cu43Nb3Co2Al4Y1La1。
Yield strength (the σ of diameter 6mm, length 9mm samples0.2) it is about 700~800MPa, shown after surrender strong
Hardening phenomenon is processed, total deformation is about 5~9%, fracture strength about 1600~1800MPa.Alloy shows super-elasticity row
For about 2~4%.During CYCLIC LOADING, alloy material shows narrow hysteresis superlastic sexual behaviour.
DSC experiments show that the solidus temperature (beginning fusion temperature) of alloy is about 850~870 DEG C, and liquidus temperature is about
For 950~970 DEG C.
Claims (6)
- A kind of 1. Zr based superelastic alloys, it is characterised in that：By atomic percentage, the Zr based superelastic alloys chemistry into It is divided into：ZraCubNbcCodAleREf, wherein：A=45~55, b=39~50, c=1~10, d=1~2, e=1~4, f=0 ~2, a+b+c+d+e+f=100；RE is the one or more in rare earth element；The alloy has super-elasticity at ambient temperature Behavior, up to 4.2%；The alloy has Thermoelastic Martensitic Transformation in A characteristic, and maximum shape memory effect is 2.1%.
- 2. Zr based superelastic alloys described in accordance with the claim 1, it is characterised in that：By atomic percentage, the Zr bases surpass The chemical composition of elastic alloy is：ZraCubNbcCodAleREf, wherein：A=46~50, b=39~49, c=1~10, d=1 ~2, e=1~4, f=0~1, a+b+c+d+e+f=100；RE is the one or more in rare earth element.
- 3. Zr based superelastic alloys described in accordance with the claim 1, it is characterised in that：The alloy answers masterpiece room temperature condition is same With it is lower repeat loading can obtain more than twice with it is narrow hysteresis superlastic sexual behaviour, i.e., maximum strain hysteresis and can recovery strain ratio Value is less than 50%.
- 4. the preparation method of Zr based superelastic alloys described in accordance with the claim 1, it is characterised in that：This method includes following step Suddenly：(1) using the metal of technical grade purity as raw material, component is weighed into mixing according to composition proportion and obtains metal mixture；(2) in an inert atmosphere, gained metal mixture is made by alloy using electric arc or induction melting method, melt back is extremely Component is uniform, obtains master alloy ingot；(3) master alloy ingot of preparation is melted by electric arc or sensing heating, utilizes copper mold casting method, vacuum water quenching method or vacuum The alloy bar material of size and dimension needed for casting die acquisition；(4) using being machined, the alloy bar material that step (3) obtains is made to the alloy sample of required shape.
- 5. according to the preparation method of the Zr based superelastic alloys described in claim 4, it is characterised in that：In step (2), foundry alloy Smelting parameter：Melting 200~700A of electric current, vacuum 10-2~10-4Pa。
- 6. according to the preparation method of the Zr based superelastic alloys described in claim 4, it is characterised in that：In step (3), prepare and close Golden technique for bar material parameter is：Vacuum 100~10-4Pa, cooling velocity 1~102K/s, alloy melt temperature for alloy melting point with Upper 50~400 DEG C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510317131.7A CN106282663B (en) | 2015-06-10 | 2015-06-10 | A kind of Zr based superelastic alloys and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510317131.7A CN106282663B (en) | 2015-06-10 | 2015-06-10 | A kind of Zr based superelastic alloys and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106282663A CN106282663A (en) | 2017-01-04 |
| CN106282663B true CN106282663B (en) | 2018-05-15 |
Family
ID=57659551
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510317131.7A Active CN106282663B (en) | 2015-06-10 | 2015-06-10 | A kind of Zr based superelastic alloys and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106282663B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110004325B (en) * | 2019-04-13 | 2020-10-20 | 常州世竟液态金属有限公司 | High-biocompatibility zirconium alloy |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1526030A (en) * | 2001-06-07 | 2004-09-01 | ��̬ͼ������˾ | Metal frame for electronic hardware and flat panel displays |
| CN1556239A (en) * | 2004-01-12 | 2004-12-22 | 大连理工大学 | Cu-Zr-Nb series block non crystalline alloy |
| CN1958831A (en) * | 2005-11-01 | 2007-05-09 | 中国科学院物理研究所 | Copper-zirconium based amorphous alloy, and preparation method |
| CN102534437A (en) * | 2011-12-15 | 2012-07-04 | 比亚迪股份有限公司 | Amorphous alloy and method for preparing same |
| CN103695814A (en) * | 2012-12-31 | 2014-04-02 | 比亚迪股份有限公司 | Zirconium based amorphous alloy and preparation method thereof |
| CN103911564A (en) * | 2012-12-31 | 2014-07-09 | 比亚迪股份有限公司 | Zr based amorphous alloy and manufacturing method thereof |
| CN104451469A (en) * | 2014-12-29 | 2015-03-25 | 东莞台一盈拓科技股份有限公司 | Amorphous alloy spectacle frame and glass and production method thereof |
| CN104498844A (en) * | 2014-11-18 | 2015-04-08 | 北京科技大学 | Heavy size TRIP amorphous composite material and preparation method thereof |
-
2015
- 2015-06-10 CN CN201510317131.7A patent/CN106282663B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1526030A (en) * | 2001-06-07 | 2004-09-01 | ��̬ͼ������˾ | Metal frame for electronic hardware and flat panel displays |
| CN1556239A (en) * | 2004-01-12 | 2004-12-22 | 大连理工大学 | Cu-Zr-Nb series block non crystalline alloy |
| CN1958831A (en) * | 2005-11-01 | 2007-05-09 | 中国科学院物理研究所 | Copper-zirconium based amorphous alloy, and preparation method |
| CN102534437A (en) * | 2011-12-15 | 2012-07-04 | 比亚迪股份有限公司 | Amorphous alloy and method for preparing same |
| CN103695814A (en) * | 2012-12-31 | 2014-04-02 | 比亚迪股份有限公司 | Zirconium based amorphous alloy and preparation method thereof |
| CN103911564A (en) * | 2012-12-31 | 2014-07-09 | 比亚迪股份有限公司 | Zr based amorphous alloy and manufacturing method thereof |
| CN104498844A (en) * | 2014-11-18 | 2015-04-08 | 北京科技大学 | Heavy size TRIP amorphous composite material and preparation method thereof |
| CN104451469A (en) * | 2014-12-29 | 2015-03-25 | 东莞台一盈拓科技股份有限公司 | Amorphous alloy spectacle frame and glass and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN106282663A (en) | 2017-01-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Bram et al. | Powder metallurgical fabrication processes for NiTi shape memory alloy parts | |
| CN107419154B (en) | One kind having hyperelastic TiZrHfNbAl high-entropy alloy and preparation method thereof | |
| CN105143482B (en) | Nickel-cobalt alloy | |
| Dehghani et al. | Hot deformation behavior of 60Nitinol (Ni60 wt%–Ti40 wt%) alloy: Experimental and computational studies | |
| Nayan et al. | Vacuum induction melting of NiTi shape memory alloys in graphite crucible | |
| CN107385365B (en) | Ti-Zr-Cu-Be quaternary amorphous composite material with work hardening capacity and preparation method thereof | |
| EP3124641B1 (en) | Method of manufacturing ni alloy part | |
| CN111411263B (en) | Low-temperature superelasticity Ti-Ni-Cu-Y-Hf shape memory alloy and preparation method thereof | |
| CN107828988A (en) | A kind of inexpensive Ti Zr based high-temperature shape memory alloys and preparation method thereof | |
| RU2698018C2 (en) | High-strength homogeneous copper-nickel-tin alloy and method for production thereof | |
| Heilmaier et al. | Order strengthening in the cast nickel-based superalloy IN 100 at room temperature | |
| Takeyama et al. | Microstructures and mechanical properties of NiAl–Ni 2 AlHf alloys | |
| Yang et al. | Effect of minor Cu content on microstructure and mechanical property of NiTiCu bulk alloys fabricated by crystallization of metallic glass powder | |
| Lee et al. | Deformation behavior of Zr-based bulk metallic glass in an undercooled liquid state under compressive loading | |
| CN106282663B (en) | A kind of Zr based superelastic alloys and preparation method thereof | |
| Kim et al. | Enhancement in strength and superelastic cyclic durability by addition of Si in Ni–Ti–Cu–Zr alloy | |
| CN110819872B (en) | Fe-Mn-Al-Ni-Nb shape memory alloy and preparation method thereof | |
| CN114855050B (en) | High-strength light-weight refractory high-entropy alloy and preparation method thereof | |
| CN109482880B (en) | Preparation method that is a kind of while promoting Ni-Mn-In alloy mechanical property and magnetic heating performance | |
| CN105886965A (en) | Element N and O co-doped ti-based amorphous composite and preparation method thereof | |
| CN111394665B (en) | TiCuZrPdFe amorphous composite material and preparation method thereof | |
| CN104419879B (en) | A kind of zirconium-base amorphous alloy with antioxygenic property and wide supercooling liquid phase region | |
| JP5929251B2 (en) | Iron alloy | |
| Hussain et al. | Effects of Different Quaternary Additions in the Properties of a Cu-Al-Mn Shape Memory Alloy | |
| Liu et al. | Thermal deformation behavior and processing maps of nickel-free high nitrogen austenitic Cr18Mn16Mo2. 5N0. 83Nb0. 15 stainless steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |