CN107523719B - A kind of novel high rigidity NiTi based alloy - Google Patents
A kind of novel high rigidity NiTi based alloy Download PDFInfo
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- CN107523719B CN107523719B CN201710867383.6A CN201710867383A CN107523719B CN 107523719 B CN107523719 B CN 107523719B CN 201710867383 A CN201710867383 A CN 201710867383A CN 107523719 B CN107523719 B CN 107523719B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
There is high rigidity, low-elasticity-modulus, rub resistance abrasion, low-density, the NiTi based alloy of nonmagnetic, corrosion resistant rich nickel the invention discloses a kind of.Replace Ti in Ni-Ti alloy Al, Nb, Hf, Ta, Zr, Mo, Co elements (X group element) or combinations thereof by being added on the basis of the Ni-Ti Binary Alloy System of rich nickel.Or addition replaces Ni in Ni-Ti alloy Cu, Fe, Cr, Mo, Co elements (Y group element) or combinations thereof on the basis of the Ni-Ti Binary Alloy System of rich nickel.Or it is added simultaneously on the basis of the Ni-Ti Binary Alloy System of rich nickel and replaces in Ni-Ti alloy Ti and Ni above-mentioned alloying elements and combinations thereof.The main reinforcing phase Ni nanoparticle of the alloy4Ti3Phase, volume fraction are 30~80Vol%, and alloy rigidity is not less than 600HV.
Description
Technical field
The present invention relates to a kind of material suitable for structure members such as bearing and gears more particularly to a kind of high rigidity, low
Play the NiTi metal alkyl materials of mould, the abrasion of corrosion-resistant and rub resistance.
Background technique
In the equipment manufactures such as Aeronautics and Astronautics, machinery, petroleum, chemical industry, electric power, ocean, there are the abrasions of a large amount of rub resistances
Metal machinery components, such as bearing or gear etc..These metal parts are needed with high rigidity, high intensity, rub resistance
Polishing machine and excellent corrosion resistance etc..Existing high rigidity bearing and gear material mostly use high-elastic mould, hard alloy
To improve its wearability and prolong the service life, such as common GCr15, M50 steel.However high-elastic mould, hard alloy are loading
In the case of, recoverable strain is usually less than 1%, once bearing military service transient state partial points meet with overload impact, bearing is high in circulation
The situations such as destructive Bu Shi impression, surface fatigue peeling easily occur under contact pressure, cause bearing and gear failure.
Current research discovery, low-elasticity-modulus, high-hardness have higher resistant to overload than traditional high rigidity, high-elastic mold materials
Damage and longer wear-out life.Low elastic modulus material can pass through high-level elastic strain and local high load phase in overload impact
It adapts to, by increasing load contact area, reduces local stress, the metal machineries components such as bearing and gear are alleviated or avoided
Surface damage improves its bearing capacity.
High rigidity NiTi based alloy is the alloy (Ni > 52at%) of richness Ni a kind of, and high Ni content makes it lose shape note
Recall characteristic, has been formed simultaneously a kind of similar to tough/hard two-phase coherence of γ in nickel base superalloy/γ ' tissue NiTi/Ni4Ti3
Structure obtains high rigidity, low-elasticity-modulus characteristic.NiTi based alloy hardness number can reach 58~62HRC, send out with current advanced aviation
Motivation is suitable with M50 bearing steel, and elasticity modulus is only half of the latter or so.NiTi based alloy compares axis as a kind of specific gravity
The light material (density about 6.7g/cm3) that steel mitigates 15% is held, it is additional in conjunction with the characteristic that high rigidity and low-elasticity-modulus are mutually matched
It can be used as it in Aeronautics and Astronautics, machinery, stone the characteristics such as immunocompetence, the non magnetic and electric conductivity of aqueous corrosion
The metal machinery components application of the rub resistances such as the equipment manufactures middle (center) bearing such as oil, chemical industry, electric power, ocean, gear abrasion.
It should be noted that another member of NiTi family is widely used marmem, the shape of NiTi alloy
Shape memory effect usually only occurs in the NiTi alloy (48~52at% of Ni content) of near atomic ratio, mainly forms and is mutually
The interphase R phase and B19 of high temperature parent phase austenite (B2 structure), low-temperature martensite phase (M) or austenite to martensite transfor mation
Phase.Materials microstructure determines that its performance, the unique shape memory effect of NiTi marmem are derived from its thermo elastic martensite
Transition process.And the phase transition temperature of NiTi alloy (Ni content > 52at%) shape memory effect of high Ni content has dropped down to -100
DEG C hereinafter, substantially eliminating martensitic traoformation, after heat treatment appropriate, the main composition of alloy is mutually austenitic matrix
The Ni of phase (B2 structure) and the in the base high density of Dispersed precipitate, nano-scale4Ti3Hardening constituent, volume fraction is according to Ni
The difference of content is up to 30~80Vol%.A large amount of nanoscale Ni4Ti3The precipitation of phase greatly enhances alloy, is protecting material
While the advantages that holding NiTi alloy low-density, super-elasticity, excellent corrosion resistance, low-elasticity-modulus, be provided with high rigidity, high abrasion it is excellent
Good characteristic, thus the NiTi alloy of high Ni content becomes one of best candidate materials of structural materials such as bearing, gear.
The factor for restricting the application of high rigidity NiTi based alloy at present is that it has heat treatment hardening crack and military service process organization moves back
Change leads to hardness sharp fall.The main hardening constituent of high rigidity NiTi based alloy is Ni4Ti3Phase, but with timeliness temperature
Degree increases and aging time extends, metastable Ni4Ti3It meets to grow up and is decomposed into Ni3Ti2Phase and Ni3Ti phase, so that alloy is hard
Degree decline.Thus the current maximum operation (service) temperature of high rigidity NiTi based alloy is 400 DEG C, and which also limits its answering in the industry
With.Therefore, it although high rigidity NiTi based alloy has the biggish potentiality as outstanding bearing material, also needs into one at present
Step improves its performance.
Summary of the invention
The present invention is on the basis of the NiTi based alloy of binary richness nickel, and the appropriate content for reducing Ni or Ti element is added
Certain Al, Nb, Hf, Ta, Zr, Mo, Co alloying element improves hard while keeping the NiTi based alloy properties of rich nickel
The characteristics such as degree, high-temperature stability, wear-resistant, corrosion-resistant；Or certain V, Cu, Hf, Fe, Cr alloying element is added, improve NiTi
The toughness of based alloy, so as to improve the processing performance of alloy.Reinforcing by the design to alloy compositions, to above-mentioned alloying element
The complex intensifying mechanism of mechanism, especially multicomponent alloy element is studied and has been verified, and the more optimal NiTi of performance is obtained
Based alloy.
The complete technical solution of the present invention includes:
A kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy be ternary or quaternary alloy, and
Dispersed precipitate has hardening constituent Ni in matrix4Ti3, group is divided into one of following scheme:
(1) Ni-Ti-Al, (2) Ni-Ti-Nb, (3) Ni-Ti-V, (4) Ni-Ti-Al-Nb, (5) Ni-Ti-Al-Hf, (6)
Ni-Ti-Al-Ta, (7) Ni-Ti-Al-Zr, (8) Ni-Ti-Nb-V, (9) Ni-Ti-Nb-Ta, (10) Ni-Ti-Hf-V, (11)
Ni-Ti-Hf-Ta, (12) Ni-Ti-V-Ta, (13) Ni-Ti-V-Zr, (14) Ni-Ti-Ta-Zr；
In above-mentioned alloy compositions, Al, Nb, Hf, V, Ta, Zr element and combinations thereof replaces the position Ti in Ni-Ti alloy,
The atom percentage content of each element are as follows: 52%≤Ni≤65%；Al, Nb, Hf, V, Ta, Zr element and combinations thereof
For 0.1%-10%；Ti is surplus.
A kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy be ternary or quaternary alloy, and
Dispersed precipitate has hardening constituent Ni in matrix4Ti3, group is divided into one of following scheme:
(1) Ni-Ti-Cu, (2) Ni-Ti-Fe, (3) Ni-Ti-Cr, (4) Ni-Ti-Mo, (5) Ni-Ti-Co, (6) Ni-Ti-
Cu-Cr, (7) Ni-Ti-Cu-Mo, (8) Ni-Ti-Cu-Co, (9) Ni-Ti-Fe-Cr, (10) Ni-Ti-Fe-Mo, (11) Ni-Ti-
Fe-Co, (12) Ni-Ti-Cr-Mo, (13) Ni-Ti-Cr-Co, (14) Ni-Ti-Mo-Co；
In above-mentioned alloy compositions, Cu, Fe, Cr, Mo, Co element and combinations thereof replaces the position Ni in Ni-Ti alloy,
The atom percentage content of each element are as follows: the total amount of remaining element Cu, Fe, Cr, Mo, Co element in addition to Ni, Ti
For 0.1%-10%；And Ni+ total amount >=52%, Ti of remaining alloying element in addition to Ni, Ti is surplus.
A kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy be quaternary or the above alloy of quaternary,
And Dispersed precipitate has hardening constituent Ni in the base4Ti3, group is divided into Ni-Ti-X-Y, wherein X is selected from Al, Nb, V, Hf, Ta, Zr
Element or combinations thereof, Y is the element or combinations thereof selected from Cu, Fe, Cr, Mo, Co；X group element replaces the Ti in Ni-Ti alloy
Position, Y group element replace the position Ni in Ni-Ti alloy；The atom percentage content of each element are as follows: 52%≤Ni+Y≤65%；X group
The content of element and Y group element is 0.1%-10%；Ti is surplus.
A kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy is five yuan or five yuan or more alloys,
And Dispersed precipitate has hardening constituent Ni in the base4Ti3, group is divided into Ni-Ti-X, wherein X is selected from Al, Nb, V, Hf, Ta, Zr member
At least three kinds in element, X group element replaces the position Ti in Ni-Ti alloy, the atom percentage content of each element are as follows: 52%≤Ni
≤ 65%, it is surplus that X group element, which is 0.1%-10%, Ti,.
A kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy is five yuan or five yuan or more alloys,
And Dispersed precipitate has hardening constituent Ni in the base4Ti3, group is divided into Ni-Ti-Y, wherein Y is selected from Cu, Fe, Cr, Mo, Co element
In at least three kinds, Y group element replace Ni-Ti alloy in the position Ni；In above-mentioned alloy, the atom percentage content of each element
Are as follows: it is surplus that 52%≤Ni+Y≤65%, Y group element, which are 0.1%-10%, Ti,.
Ni in the NiTi based alloy4Ti3For hardening constituent having a size of nanoscale, volume fraction is 30~80Vol%.
The NiTi based alloy hardness is not less than 600HV.
The present invention compared with the existing technology the advantages of be:
1. the design of alloying component, firstly, having separately designed addition on the basis of the Ni-Ti Binary Alloy System of rich nickel
Replace Ti Al, Nb, Hf, Ta, Zr, Mo, Co elements in Ni-Ti alloy, and combinations thereof alloy compositions system, to increase nickel
The thermal stability of titanium-base alloy and apply temperature, further increase the performances such as hardness.Secondly, on the basis of Binary Alloy System
On, separately designed to be added and replace Ni V, Cu, Hf, Fe, Cr elements in Ni-Ti alloy, and combinations thereof alloy compositions body
System, to improve the toughness and processing performance of NiTi based alloy.Furthermore on the basis of Binary Alloy System, separately designs and added
Enter while replacing Ni and Ti in Ni-Ti alloy above-mentioned alloying element, and combinations thereof alloy compositions system, to reach comprehensive
The best match of performance.Linked groups have been researched and analysed by calculating, design and experiment for above-mentioned each alloy element, it is right
The complex intensifying mechanism of the strengthening mechanism of alloying element, especially multicomponent alloy element is studied and has been verified, and has been obtained not
With the reasonable content of alloy element.
2. the present invention, on the basis of the design of above-mentioned alloy compositions, further by alloyage process, adjustment NiTi base is closed
Main Ni in gold4Ti3Form, size, distribution and the volume fraction of nano-strengthening phase, and adjust the heat treatment of NiTi based alloy
Process window further optimizes performance.Compared with the high-elastic mold materials of traditional high rigidity, high rigidity NiTi based alloy has
The characteristics of high resiliency low modulus, higher load and wear-out life can be born.In addition to this, the NiTi based alloy of rich nickel has close
The good characteristics such as low, nonmagnetic, corrosion-resistant are spent, the rub resistances such as traditional bearing steel abrasion components are significantly better than.
Detailed description of the invention
Fig. 1 is 1050 DEG C of Ni-Ti-Al alloy of the present invention, and 3h is dissolved state and 400 DEG C, and 3h aging state micro-vickers hardness is bent
Line.
Fig. 2 is 500 DEG C of Ni-Ti-Al alloy (a) of the present invention, 1h, for 24 hours, 48h and 96h aging state micro-vickers hardness song
Line；(b) 600 DEG C, 1h, for 24 hours, 48h and 96h aging state micro-vickers hardness curve.
Fig. 3 is the transmission electron microscopy figure of NiTi alloy, wherein (a) and (b) is respectively bianry alloy Ni50.9Ti49.1Alloy
Bright field image and dark field image；(c) and (d) is respectively bianry alloy Ni55Ti45The bright field image and dark field image of alloy；(e) divide with (f)
It Wei not ternary alloy three-partalloy Ni55Ti38Al6The bright field image and dark field image of alloy.
Fig. 4 is several typical embodiment Ni of the present invention54Ti42Al4、Ni53Ti38Al3Hf4Mo2、Ni55Ti40Nb5、
Ni52Ti44Al4And Ni51Ti40Hf5Cu41050 DEG C of alloy, 3h is dissolved sample compression stress-displacement curve.
Fig. 5 is several typical embodiment Ni of the present invention55Ti39Al6、Ni52Ti44Al4、Ni52Ti40Hf5Cr3、
Ni52Ti38Al2Hf5Cu3And Ni53Ti38Al3Hf4Mo21050 DEG C of alloy, 3h is dissolved sample three-point bending fracture toughness.
Specific embodiment
The present invention is further elaborated below in conjunction with example, but the invention is not limited to specific embodiments.
The raw materials used titanium sponge (Ti) including purity 99.76% (wt.%) of the specific embodiment of the invention, 99.98%
(wt.%) aluminium ingot (Al) of nickel block (Ni), 99.99% (wt.%), the niobium sheet (Nb) of 99.99% (wt.%), 99.95%
(wt.%) the vanadium particle (V) of Hf stick, 99.95% (wt.%), 99.95% (wt.%) tantalum block, 99.95% (wt.%) zirconium
Particle (Zr), the copper billet (Cu) of 99.99% (wt.%), the iron block (Fe) of 99.95% (wt.%), 99.95% (wt.%) chromium
The cobalt granule (Co) of block (Cr), the molybdenum grain (Mo) of 99.99% (wt.%) and 99.95% (wt.%).
Raw material surface is cleaned before preparing (including pickling, alkali cleaning scale removal, using acetone and/or alcohol
Degrease) and polishing, drying and processing then is carried out to raw material, is weighed after drying with high Accuracy Electronic Balance.
The alloy material of ingredient is formulated as follows by 1 nominal composition of table:
The ingredient lists of 1 embodiment 1-20 of table (constituent content is atomic percent at.%)
Vacuum non-consumable electric arc melting, vacuum induction melting, vacuum magnetic suspension melting and double vacuum can be used in the alloy
The uniform NiTi based multicomponent alloy ingot of any prepared composition in the methods of (vacuum induction+vacuum consumable).The present invention is specific
The raw material for preparing weight is fitted into the water jacketed copper crucible of vacuum non-consumable arc furnace by embodiment, then covers sealing cover, is taken out
Vacuum is to 3~5 × 10-3After Pa, being filled with high-purity argon gas makes vacuum degree 0.05MPa, then melts repeatedly under argon atmosphere protection
4~5 times are refined to ensure that ingredient is uniform, is taken out after finally cooling to room temperature with the furnace, is smelted into typical button shape ingot casting.
The alloy homogenizing annealing temperature is chosen as 950~1100 DEG C, soaking time 2~24 hours；Solid solubility temperature is optional
Water quenching after being 950 DEG C~1200 DEG C, soaking time 2~8 hours；Aging temp is chosen as 350 DEG C~650 DEG C, and soaking time 1~
100 hours.Ingot casting is put into vacuum heat treatment furnace and carries out homogenizing annealing, annealing temperature 1050 by the specific embodiment of the invention
DEG C, furnace cooling after heat preservation 24 hours.The pole for cutting φ 5mm from above-mentioned ingot casting using wire cutting machine, is encapsulated in quartzy glass
In glass pipe, 10 are evacuated in glass tube-3Argon gas is filled with as protective gas after Pa grades of vacuum degree.Sample after tube sealing is common
1050 DEG C/3h solid solution is carried out in tube furnace, and alloy is heat-treated by 2 institution of prescription of table after water quenching.
The aging strengthening model system of 2 alloy of table
Use the microscopic structure of electron probe and transmission electron microscope observation alloy.It is tested using micro Vickers
The Vickers hardness of alloy obtained above, to avoid deviation caused by nonuniform organization, ten groups of data of each sample test are calculated
Average value.
Using wire cutting method, diameter d=5mm will be cut in alloy obtained above, the cylindrical body of height h=8mm is made
For Mechanics Performance Testing sample, compression pressure-strain testing, compression are carried out using SANGS 100KN type universal material experimental machine
Strain rate is 0.2mm/min.
Long L=30mm, wide W=6mm, high H=3mm are cut using wire cutting granting, prefabricated notch length B=1.5mm's
Cuboid sample is as fracture toughness test sample.3 points of curved tests are carried out using SANGS 100KN type universal material experimental machine,
Strain rate is 0.1mm/min.
The mechanical property table of embodiment 1-20 such as table 3:
The mechanical property table of 3 embodiment 1-20 of table
As can be seen from Table 3, the hardness of alloy and strong can be improved in the addition of alloy element Al, Nb, Ta, Zr, Mo, Co
The toughness of alloy can be improved in degree, the addition of alloying element Hf, Cu, V, Fe, Cr.Ni content is higher, and the hardness of alloy is higher, drop
The toughness of alloy can be improved in low Ni content.
As seen from Figure 1, the hardness of alloy is increased with the increase of Al content, and Ni-Ti-Al ternary alloy three-partalloy exists
There is apparent hardness to be promoted after 400 DEG C of timeliness.Fig. 2 be 500 DEG C of 55Ni-45Ti bianry alloy and Ni-Ti-Al ternary alloy three-partalloy and
600 DEG C of high temperature long-time timeliness hardness curves, Bimary and trinary alloy can keep at least 96h long Shi Wending, but three at 500 DEG C
The hardness of first alloy is significantly higher than bianry alloy；Aging temp is further increased to 600 DEG C, Ni-Ti-Al ternary alloy three-partalloy is able to maintain
High rigidity is declined slightly but can still be higher than 700HV when 96h to, continuing to extend for 24 hours time hardness, and bianry alloy hardness is sharply
Only 400HV or so is dropped to, this is because Ni4Ti3 strengthens phase decomposition.
The shape of nickelic Nitinol (Fig. 3 c-f) and near atomic ratio it can be seen from Fig. 3 transmission electron microscopy figure
Memorial alloy (Fig. 3 a-b) microscopic structure is significantly different.Ni in the bright of Nitinol of binary richness nickel, dark field image4Ti3It is mutually in convex lens
Mirror body (Fig. 3 c-d), having a size of 100-200nm (draw ratio 2:1 to 5:1).(Fig. 3 e-f) after Al is added to refine main hardening constituent
Ni4Ti3, Ni4Ti3Mutually be it is coccoid, size is less than 10nm, therefore the hardness and strength of alloy can be improved.
Fig. 4 is the compression curve of several exemplary embodiments, it can be seen from the figure that reducing Ni content can be improved alloy
The addition of plasticity, alloying element Hf, Cu can also be improved plasticity.
Fig. 5 is the fracture toughness histogram of several exemplary embodiments, it can be seen from the figure that reducing Ni content can be improved
The addition of the fracture toughness of alloy, alloying element Hf, Cu can also be improved toughness.
Friction-wear test carries out on UMT-2 type friction wear testing machine, and lubricating condition is dry friction, using ball-disk
Contact carries out reciprocating friction wear test, and the secondary upper sample that rubs usesSi3N4Ball, lower sample are closed according to table 1
Golden component processingAlloy disc, load 20N, frequency 5Hz, step-length 6mm, wearing- in period 4h.It is with sensibility reciprocal
The assay balance of 0.1mg weighs the quality of time abrasion front and back, and the difference of the two is abrasion loss.
Friction and wear test result such as table 4:
The friction and wear behavior table of 4 embodiment 1-20 of table
| Embodiment number | Abrasion loss/mg | Coefficient of friction |
| 1 | 1.2 | 0.07 |
| 2 | 2.3 | 0.12 |
| 3 | 2.8 | 0.14 |
| 4 | 2.2 | 0.11 |
| 5 | 1.9 | 0.10 |
| 6 | 2.0 | 0.09 |
| 7 | 1.5 | 0.08 |
| 8 | 1.9 | 0.10 |
| 9 | 1.3 | 0.07 |
| 10 | 2.0 | 0.11 |
| 11 | 2.5 | 0.12 |
| 12 | 1.9 | 0.09 |
| 13 | 2.1 | 0.11 |
| 14 | 2.1 | 0.12 |
| 15 | 1.9 | 0.08 |
| 16 | 1.8 | 0.08 |
| 17 | 1.9 | 0.09 |
| 18 | 2.0 | 0.10 |
| 19 | 1.9 | 0.10 |
| 20 | 1.8 | 0.09 |
As can be seen from Table 4, alloy rigidity is higher, and abrasion loss is smaller, and coefficient of friction is also smaller, therefore friction and wear behavior
Better.Embodiment 1-20 has good antiwear property, can be used for preparing anti-friction bearing product.
Electrochemical corrosion test is carried out using the sample of 15 × 15 × 5mm of wire cutting, the NaCl that corrosive medium is 3.5% is molten
Liquid.
Electrochemical corrosion test result such as table 5:
The electrochemical parameter table of 5 embodiment 1-20 of table
| Embodiment number | Corrosion potential (V) | Passivation current (A/cm2) | Corrosion rate (mm/a) |
| 1 | -0.452 | 2.38×10-10 | 2.44×10-6 |
| 2 | -0.415 | 2.54×10-10 | 2.52×10-6 |
| 3 | -0.404 | 2.78×10-10 | 2.89×10-6 |
| 4 | -0.585 | 1.61×10-10 | 1.25×10-6 |
| 5 | -0.506 | 1.89×10-10 | 1.58×10-6 |
| 6 | -0.630 | 1.52×10-10 | 1.17×10-6 |
| 7 | -0.496 | 1.95×10-10 | 1.92×10-6 |
| 8 | -0.485 | 1.98×10-10 | 1.85×10-6 |
| 9 | -0.492 | 1.93×10-10 | 1.75×10-6 |
| 10 | -0.412 | 2.99×10-10 | 3.13×10-6 |
| 11 | -0.461 | 2.24×10-10 | 2.39×10-6 |
| 12 | -0.480 | 2.07×10-10 | 2.01×10-6 |
| 13 | -0.473 | 2.12×10-10 | 2.19×10-6 |
| 14 | -0.443 | 2.32×10-10 | 2.43×10-6 |
| 15 | -0.430 | 2.51×10-10 | 2.57×10-6 |
| 16 | -0.534 | 1.76×10-10 | 1.38×10-6 |
| 17 | -0.689 | 1.25×10-10 | 1.05×10-6 |
| 18 | -0.416 | 2.58×10-10 | 2.60×10-6 |
| 19 | -0.482 | 2.05×10-10 | 2.11×10-6 |
| 20 | -0.482 | 1.96×10-10 | 1.87×10-6 |
Corrosion potential is lower, and passivation current is lower, and corrosion rate is lower, then corrosion resistance is better.It can be seen by table 5
Out, the corrosion resistance sequence of alloying element is as follows: Cr > Nb > Hf > Fe > Co > Cu > Al > Ta > Zr > Mo > V.Alloy Ni content is got over
Height, corrosion resistance are better.
The above description is only a preferred embodiment of the present invention, is not intended to limit the scope of the invention, all utilizations
Equivalent structure or equivalent flow shift made by present specification is applied directly or indirectly in other relevant technologies
Field is included within the scope of the present invention.
Claims (5)
1. a kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy is ternary or quaternary alloy, and in base
Dispersed precipitate has hardening constituent Ni in body4Ti3, group is divided into one of following scheme:
(1) Ni-Ti-Al, (2) Ni-Ti-Nb, (3) Ni-Ti-V, (4) Ni-Ti-Al-Nb, (5) Ni-Ti-Al-Hf, (6) Ni-
Ti-Al-Ta, (7) Ni-Ti-Al-Zr, (8) Ni-Ti-Nb-V, (9) Ni-Ti-Nb-Ta, (10) Ni-Ti-Hf-V, (11) Ni-
Ti-Hf-Ta, (12) Ni-Ti-V-Ta, (13) Ni-Ti-V-Zr, (14) Ni-Ti-Ta-Zr；
The atom percentage content of each element are as follows: 52% < Ni≤65%；Al, Nb, Hf, V, Ta, Zr element and combinations thereof is
0.1%-10%；Ti is surplus.
2. a kind of high rigidity NiTi based alloy, which is characterized in that the NiTi based alloy is five yuan or five yuan or more alloys, and
Dispersed precipitate has hardening constituent Ni in the base4Ti3, group is divided into Ni-Ti-X, wherein X is selected from Al, Nb, V, Hf, Ta, Zr element
In at least three kinds；
The atom percentage content of each element are as follows: it is surplus that 52% < Ni≤65%, X group element, which are 0.1%-10%, Ti,.
3. -2 described in any item NiTi based alloys according to claim 1, which is characterized in that in the NiTi based alloy, Al,
Nb, Hf, V, Ta, Zr element and combinations thereof replaces the position Ti in Ni-Ti alloy.
4. -2 described in any item NiTi based alloys according to claim 1, which is characterized in that in the NiTi based alloy
Ni4Ti3For hardening constituent having a size of nanoscale, volume fraction is 30~80Vol%.
5. -2 described in any item NiTi based alloys according to claim 1, which is characterized in that the NiTi based alloy hardness is not
Lower than 600HV.
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| CN110923508A (en) * | 2019-12-12 | 2020-03-27 | 哈尔滨工程大学 | NiTiHfSc high-temperature shape memory alloy and preparation method thereof |
| CN114351005B (en) * | 2022-01-20 | 2022-06-17 | 希罗镜下医疗科技发展(上海)有限公司 | Method for synthesizing substrate material by using nickel-titanium metal |
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