CN105908000A - Light high-strength and high-tenacity NiTi shape memory alloy composite damping material with wide temperature range and preparing method and application thereof - Google Patents
Light high-strength and high-tenacity NiTi shape memory alloy composite damping material with wide temperature range and preparing method and application thereof Download PDFInfo
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- CN105908000A CN105908000A CN201610436782.2A CN201610436782A CN105908000A CN 105908000 A CN105908000 A CN 105908000A CN 201610436782 A CN201610436782 A CN 201610436782A CN 105908000 A CN105908000 A CN 105908000A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/11—Making porous workpieces or articles
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/11—Making porous workpieces or articles
- B22F3/1121—Making porous workpieces or articles by using decomposable, meltable or sublimatable fillers
- B22F3/1125—Making porous workpieces or articles by using decomposable, meltable or sublimatable fillers involving a foaming process
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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Abstract
The invention discloses a light high-strength and high-tenacity NiTi shape memory alloy composite damping material with a wide temperature range and a preparing method and application thereof. The method comprises the following steps: uniformly mixing pure nickel powder and pure titanium powder according to an atomic ratio of (100-x):x, wherein x is 52 to 64; pressing mixed powder into a shape so as to obtain a green body; placing the pressed green body in a high-temperature furnace, vacuuming to smaller than 0.01pa, filling shielding gas to carry out shielded sintering, and controlling that sintering is carried out at a temperature of 1000-1200 DEG C for 5-20 hours; and after finishing sintering, cooling a product to a room temperature with the furnace so as to obtain a light high-strength and high-tenacity NiTi shape memory alloy composite damping material compositing a second phase and pores. The material has high strength, high tenacity, a high damping property and wide use temperatures and is particularly suitable for being used as a damping, sound insulating and impact-resistant material on a machine used in a severe environment.
Description
Technical field
The present invention relates to high-strength and high ductility composite damping material field, be combined with hole particularly to a kind of second phase
High-strength light NiTi marmem damping material and preparation method and application.
Background technology
Noise and vibration, impact failure are in a lot of fields, such as Aero-Space, and military affairs, transportation, building etc.,
Generally existing, and unavoidably, this brings numerous baneful influence to all trades and professions, the most serious after
Really.On the one hand the precision of equipment, life and reliability, serious caused expensive equipment loss of function are affected；
On the other hand aggravating working environment, the health and lives of harm people.Noise and vibration and impact failure at present controls
The industry development in field is rapid, since recent decades, has increasingly received significant attention, and the market demand is all
It is incremented by a high speed year by year.And solution mainly has three kinds at present, one is to increase quality and the rigidity of structure,
Reduce amplitude；Two is to reduce mesomerism；Three is to use high damping material to realize damping energy-absorbing.In view of one
The wide temperature range (100～200 DEG C) in the fields such as a little bullet train, urban construction, tank armor, submarines makes
With environment, and require material have high intensity, higher toughness and plasticity, corrosion resistance, fire protecting performance and
The characteristics such as long-life, organic viscoelastic material lacks due to its low melting point, low-intensity and not reproducible use etc.
Point, has been no longer appropriate for using at these special occasions, has developed high damping alloy material imperative.Mesh
Front conventional high damping alloy has four big classes, magnesium alloy high-strength light, but corrosion resistance is poor；Ferromagnetic type
The cheap intensity of alloy is high, but affected by magnetic fields seriously, application scenario is greatly limited；Complex phase type
Casting pig and allumen damping performance are poor, and intensity is low, is not suitable for applied at elevated temperature.Marmem relies on
The viscosity energy-absorbing of Interface Motion, high-damping height is tough, and deformation can recover, and cyclic deformation ability is good, makes
Obtain it and have huge application prospect in damping anti-noise, shock resistance field.
At present, in the memorial alloy (mainly including NiTi base, Cu base and Fe yl) having been developed over,
NiTi memorial alloy is considered as the one of most using value, this is because it has the comprehensive mechanics of optimum
Performance, stable shape memory effect and super-elasticity, excellent corrosion-resistant and fatigue behaviour.This makes NiTi
Memorial alloy at industrial circle and biomedical sector, has a wide range of applications.But, numerous
Application scenario also requires parts lightweight, to reach to save the purpose of the energy.Therefore, research is had to be drawn by hole
Enter in porous NiTi memorial alloy, thus prepare porous NiTi shape memory alloy, alleviate weight with this
Amount.Meanwhile, when porous material is destroyed by foreign impacts, it is possible to use the bending of its hole rib and caving in
Also can consume big energy, and also have a wide range of applications in damping noise reduction and shock resistance field.But, hole
The introducing of gap can reduce intensity and the plasticity of porous NiTi memorial alloy, particularly under high porosity, its
Intensity is the lowest, and material becomes the most crisp, the advantage losing fine and close the had high-strength and high ductility of NiTi alloy.
Second phase and hole can be combined introducing NiTi marmem, prepare high-strength and high-ductility
Light porous NiTi shape memory alloy, and damping capacity is excellent, this will have important
Using value.
Summary of the invention
In order to overcome the shortcoming of prior art with not enough, it is an object of the invention to provide a kind of second phase and hole
Lightweight high-damping NiTi shape memory alloy that gap is compound and preparation method thereof, in wide temperature range
(100 DEG C～200 DEG C) all represent the damping capacity of high intensity, high-ductility and excellence.
The lightweight high-damping NiTi shape memory that another object of the present invention is to provide said method to obtain closes
The application of metal/composite material.
The purpose of the present invention is achieved through the following technical solutions:
The preparation method of wide temperature range high-strength light high-ductility NiTi marmem composite damping material, including
Following steps:
(1) mixed powder: pure nickel powder and pure titanium valve are pressed atomic ratio (100 x): x mix homogeneously, x is 52～64；
The powder pressing forming that will mix, obtains green compact；
(2) sintering: the green compact that step (1) suppresses are put in high temperature furnace, is first evacuated to 0.01Pa
Hereinafter, being filled with protective gas and carry out protection sintering, controlling sintering temperature is 1000～1200 DEG C, sintering time
Being 5～20 hours, after having sintered, product cools to room temperature with the furnace, obtains the second phase and hole compound
High-strength light high-ductility NiTi marmem composite damping material.
For realizing the object of the invention further, it is preferable that the purity more than 99.5% of described pure titanium valve,
Particle size 50～75 μm；The purity more than 99.5% of described pure nickel powder, particle size is 50～75 μm.
Preferably, step (1) described mixing is to use ball-milling method or conventional powder mixing method to mix.
Preferably, step (1) described compressing be use die pressing carry out；Described compressing pressure
Power is 50～600MPa, and temperature is 30～100 DEG C, time 3～15 minutes.
Preferably, step (1) green compact also include pore creating material；Pore creating material feed postition is pure nickel powder and pure
Titanium valve is by atomic ratio (100 x): include adding pore creating material, pore creating material and NiTi mixed powder after x mix homogeneously
Mix homogeneously, or pure nickel powder and pure titanium valve and pore creating material mix homogeneously；The powder compacting that will mix
Molding, obtains green compact；Described pore creating material is ammonium hydrogencarbonate or carbamide, purity more than 99%, granule chi
Very little 100～500 μm；The addition of pore creating material is the 0～50% of NiTi mixed powder quality；Add pore creating material and
The green compact suppressed are put in high temperature furnace, are first evacuated to below 0.01Pa, and are always maintained at vacuum,
Then presintering is carried out except pore creating material, it is thus achieved that porous green compact re-sinter.
Preferably, described pre-sintering temperature 200 250 DEG C, the presintering time is 0.1～5 hour.
Preferably, described high temperature furnace is low-pressure sintering furnace or vacuum tube furnace.
Preferably, described protective gas is argon；The air pressure of protective gas is 300Pa～4MPa.
A kind of wide temperature range high-strength light high-ductility NiTi marmem composite damping material, by above-mentioned preparation
Method prepares；Material is 76～1620MPa the compressive strength of 100 DEG C～200 DEG C, and compressible strain is
10～32%, damped coefficient is 0.025～0.08；Material has 10～the porosity of 60% and 100～500 μm
Hole, the density of material is less than 5g/cm3.Above-mentioned material feature shows material width temperature range high-strength and high ductility, close
Degree is less than 5g/cm3Show that material is light material.
Described wide temperature range high-strength light high-ductility NiTi marmem composite damping material is as automobile or boat
Energy-absorbing on it device and the application of protecting against shock parts, or as tank or the sound-absorbing of submarine, vibration isolation and protecting against shock
The application of material.
The principle of the present invention is: utilize Ni element and Ti element reaction sintering can form NiTi phase, simultaneously
The difference of the interdiffusion coefficient between Ni and Ti element, can form Ke Kendaer hole, thus obtain light
Matter porous NiTi alloy；And, increase porosity further also by adding pore creating material.By controlling
Sintering process parameter, such as different molding pressures, sintering pressure, sintering temperature and sintering time etc., can adjust
Porosity, pore appearance, pore size and the connectedness etc. of whole porous NiTi memorial alloy.Mostly important
, according to Ni Ti binary phase diagraml, in given atomic ratio interval, Ti can be separated out at TiNi phase situ2Ni
Second phase, thus fragility Ti is prepared when sintering completes2Ni intermetallic compound and toughness TiNi phase compound
Material.Utilize high-strength Ti2Ni phase and the Coupling with Mechanics of toughness TiNi phase and interface interaction, thus prepare
High-strength, the NiTi marmem composite damping material of high-ductility.
Hinge structure of the present invention has such advantages as and beneficial effect:
1) the wide temperature range high-strength light high-ductility NiTi marmem composite damping material of the present invention has
10～the porosity of 60% and the hole of 100～500 μm, and show high compressive strength
(76～1620MPa), high compressible strain (10～32%)；Damped coefficient is high (0.025～0.08), and
The temperature range of application is broad (100 DEG C～200 DEG C)；Excellent combination property, is particularly well-suited to aviation, smooth
Gram, the damping in the field such as submarine, bullet train, sound insulation, the parts of protecting against shock.
2) present invention utilizes Ni Ti bianry alloy own characteristic, must generate in special component scope
Ti2Ni's and NiTi is composite phase-structured, in combination with the powder metallurgy process of technical maturity.Therefore the present invention
Technique is simple, reliable, success rate is high.
Accompanying drawing explanation
Fig. 1 is the macroscopical sample drawing after embodiment 1 alloy sample sintering；
Fig. 2 is the metallograph of embodiment 1 alloy sample；
Fig. 3 is that the heat of embodiment 1 alloy sample analyzes (DSC) curve；
Fig. 4 is material phase analysis (XRD) diffraction curve of embodiment 1 alloy sample；
Fig. 5 is scanning electron microscope high power (a) and low power (b) photo of embodiment 1 alloy sample；
Fig. 6 is room temperature and high temperature (130 DEG C) the compression failure curve of embodiment 1 alloy sample；
Fig. 7 is the damping temperature spectrogram continuously of embodiment 1 alloy sample；
Fig. 8 is the metallograph of embodiment 2-in-1 gold sample；
Fig. 9 is scanning electron microscope high power (a) and low power (b) photo of embodiment 2-in-1 gold sample；
Figure 10 is the room temperature compression failure curve of embodiment 2-in-1 gold sample；
Figure 11 is embodiment 2-in-1 gold high-temperature sample (130 DEG C) compression reaction curve (1%～8%)；
Figure 12 is the damping temperature spectrogram continuously of embodiment 2-in-1 gold sample；
Figure 13 is scanning electron microscope high power (a) and low power (b) photo of embodiment 3 alloy sample；
Figure 14 is the room temperature compression failure curve of embodiment 3 alloy sample；
Figure 15 is the damping temperature spectrogram continuously of embodiment 3 alloy sample；
Figure 16 is the metallograph that embodiment 4 adds up to sample；
Figure 17 is scanning electron microscope high power (a) and low power (b) photo of embodiment 4 alloy sample；
Figure 18 is the room temperature compression failure curve of embodiment 4 alloy sample；
Figure 19 is the damping temperature spectrogram continuously of embodiment 4 alloy sample.
Detailed description of the invention
For being more fully understood that the present invention, below in conjunction with embodiment and accompanying drawing, the present invention is made the most detailed
Describe, but embodiments of the present invention are not limited to this.
Embodiment 1
(1) pure nickel powder and pure titanium valve are pressed atomic ratio 46:54 by ball-milling method mix homogeneously, powder used
Purity is all more than 99.5%, and particle size is 50～75 μm；Then the Ni Ti powder compacting that will mix
Molding obtains green compact, press power 50MPa, press temperature 30 DEG C, 5 minutes press times；
(2) green compact that (1st) step suppresses are put in vacuum high temperature furnace, be first evacuated to 0.01Pa
Hereinafter, being then re-filled with Ar-sintering, being passed through ar pressure is 400Pa, sintering temperature 1050 DEG C,
Sintering time 5h, the high-strength light high-ductility NiTi marmem obtaining the second phase compound with hole is combined
Damping material.
Fig. 1 is lightweight Ni that prepared original position the second phase of sintering is compound with hole46Ti54Memory alloy specimen,
Surface-brightening also distributes metallic luster, measures this example by relative density method and prepares the porosity of sample and is
36.4%.The metallographic structure of this sample at room temperature observed by the DMI3000M optical microscope using Lycra,
As shown in Figure 2, it is seen that the distribution of pores of the less rule of 100～about 300um is on matrix material.Right
Transformation behavior and the phase transition temperature of sample is analyzed (as shown in Figure 3), and (transformation behavior is to use differential to sweep
Retouching calorimeter dsc measurement to go out sample and vary with temperature and change curve that heat occurs, temperature rate is
10 DEG C/min, the scope of measurement is-50 to 200 DEG C, and uses tangential method to determine its phase transition temperature), find to add
Hot and cold but time have obvious neither endothermic nor exothermic peak, this shows that sample there occurs martensitic phase transformation, and measures
The phase transition temperature that sample is concrete: Mf=40 DEG C, Ms=70 DEG C, As=75 DEG C, Af=100 DEG C.As shown in Figure 4,
Thing phase composition under this sample room temperature is mainly martensite NiTi phase and Ti2Ni phase (Fig. 4 Analysis of components
It is that the energy dissipation spectrum EDS device using scanning electron microscope subsidiary determines).In order to more preferably observe
Ti2Ni phase distribution situation in NiTi matrix, its high power (3000 times) and low power (500 times) scanning
Shown in electromicroscopic photograph such as Fig. 5 (a) and 5 (b), can clearly can be seen that Ti from figure2(size is in 2～3 μm for Ni phase
Left and right) being distributed on NiTi phase matrix of even dispersion, this structure is the second phase in situ and is combined with hole
Structure.
It is compressed test, it is thus achieved that this sample is at room temperature and high temperature (130 DEG C) according to ASTM E9 89a standard
Compression stress strain curve as shown in Figure 6, it can be seen that at room temperature its compressed rupture strength is high
Reach 712MPa, and before its fracture, strain is 32%；At high temperature its fracture strength is reduced to 460MPa,
But before its fracture, strain also can reach 30%, shows that this sample at room temperature has high intensity, and at height
The plasticity of excellence is all represented under low temperature.Fig. 7 is that the temperature curve that damps continuously under 1.2% strain amplitude (is adopted
With dynamic mechanical analysis instrument Q800, under single cantilever beam pattern, 1Hz, with 5 DEG C/min speed from
100 200 DEG C of measurements), it can be seen from figure 7 that this sample shows higher under whole temperature range
Damped coefficient, the damped coefficient in high temperature austenite state is all up 0.026, and this is than any fine and close shape
The damping of memorial alloy will be high；Meanwhile, the damped coefficient in low-temperature martensite phase is more up to 0.065.
Prepared by this example is formed in situ lightweight high-damping Ni that the second phase is compound with hole46Ti54Memorial alloy can be used
Doing structural member and shock absorber part on the equipment that the vibrations such as plate armour, submarine are big, energy absorption performance is good.
According to Ni Ti binary phase diagraml, the atomic ratio of Ti and Ni given in the present embodiment is 54:46, is burning
Ti can be separated out at TiNi phase situ when having tied2Ni the second phase, and prepared fragility Ti2Ni intermetallic
Thing and the composite of toughness TiNi phase.Meanwhile, Ni element and Ti element reaction sintering can form NiTi
Phase, due to the difference of the interdiffusion coefficient between Ni and Ti element, can form Ke Kendaer hole；And
And, under the cold pressure of 50MPa, obtaining green compact there is more hole, these holes are at 1050 DEG C of sintering
Still can remain quite a few hole after time 5h, thus obtain the porous NiTi that porosity is 36.4%
And Ti2The composite of Ni.Due to high-strength Ti2Ni phase and the Coupling with Mechanics of toughness TiNi phase and interface are made
With, thus obtain the NiTi shape memory alloy of high-strength, high-ductility and high-damping.
The sample test method and apparatus of example below is with embodiment 1.
Embodiment 2
(1) pure nickel powder and pure titanium valve are pressed atomic ratio 46:54 powder mixing method mix homogeneously routinely, powder used
The purity at end is all more than 99.5%, and particle size is 50～75 μm；Then the powder mixed is pressed into
Type obtains green compact, press power 100MPa, press temperature 50 DEG C, 15 minutes press times；
(2) green compact that (1st) step suppresses are put in high temperature furnace, are first evacuated to below 0.01Pa,
Then being re-filled with Ar-sintering, being passed through ar pressure is 1000Pa, sintering temperature 1150 DEG C, sintering
Time 10h, obtains the high-strength light high-ductility NiTi marmem composite damping that the second phase is compound with hole
Material.
The porosity measuring the sample that this example prepares by relative density method is 36%, and Fig. 8 is the gold of this sample
Phase photo, is dispersed with the hole about 100～300 μm on matrix material, prepares porous sample.For
Clearer observation Ti2The size of Ni phase and distribution situation, the such as Fig. 9 of the microstructure under scanning electron microscope
In shown in (a) and (b), it can be seen that Ti2Ni phase (size is about 4～5 μm) is evenly distributed on NiTi phase
On matrix.Comprehensive above analysis, this sample is for being formed in situ Ti2The porous NiTi note that Ni phase is compound with hole
Recall alloy composite materials.
The mechanical property of this porous NiTi composite and super-elasticity curve, as shown in FIG. 10 and 11.It
Compressive strength limit reach 620MPa, strain reaches 19%, and Figure 10 shows that this sample represents good moulding
Property and high intensity；When 130 DEG C, (martensite reverses height AfAbove) high temperature compressed return curve (from
1%～8%), seeing Figure 11, this sample can also be replied completely when prestrain 3%, shows that this material has well
Super-elasticity and toughness；Analyzed its damping capacity by dynamic thermomechanical analysis apparatus, Figure 12 is strain
Amplitude is continuous temperature damping spectrum when 1.2%, as seen from Figure 12 in high temperature austenite state, this sample
Damped coefficient can reach 0.02；At low-temperature martensite state damped coefficient up to 0.06, interval in different temperatures
Its damping capacity lower is the most fabulous.
Embodiment 3
(1) pure nickel powder and pure titanium valve are pressed atom 42:58 by ball milling powder mixing method mix homogeneously, powder used
Purity be all more than 99.5%, particle size is 50～75 μm；Then the powder pressing forming that will mix
Obtain green compact, press power 400MPa, press temperature 30 DEG C, 5 minutes press times；
(2) green compact that (1st) step suppresses are put in high-temperature low-pressure sintering furnace, be first evacuated to 0.01Pa
Hereinafter, being then re-filled with Ar-sintering, being passed through ar pressure is 4MPa, and pressurize sinters, sintering temperature
Spend 1000 DEG C, sintering time 20h, obtain the high-strength light high-ductility NiTi shape that the second phase is compound with hole
Memorial alloy composite damping material.
The porosity of this example is 10.6%, and pore-size is probably about 5 10 μm.To this sample
Phase transition temperature be analyzed, find that heating and cooling there occurs martensitic phase transformation, and determine the phase transformation of sample
Temperature is: Mf=50 DEG C, Ms=70 DEG C, As=80 DEG C, Af=105 DEG C.XRD analysis shows, this sample room
Temperature phase consists of Ti2Ni phase and martensite NiTi phase.From high power and low power stereoscan photograph, such as Figure 13
Shown in (a) and (b), it can be seen that Ti2Ni phase (its size is 5～6 μm) is linked to be netted, uniformly divides
Cloth, on NiTi matrix, shows that this sample is for being formed in situ Ti2The NiTi memorial alloy that Ni phase is compound with hole
Composite.And, the compression stress strain curve of this sample, as shown in figure 14, it can be seen that this sample
Product have the highest compressed rupture strength (1620MPa), and under higher intensity, plasticity also can also reach
10%.When strain amplitude is 0.5%, it damps temperature curve continuously and sees Figure 15, high temperature austenite state
Damping value up to 0.01；The damping of low-temperature martensite state is up to 0.025.
Embodiment 4
(1) pure nickel powder and titanium valve are pressed atomic ratio 46:54 powder mixing method mix homogeneously routinely, powder used
Purity be all more than 99.5%, particle size is 50～75 μm；Then, add in NiTi mixed powder
The ammonium hydrogen carbonate (purity 99%, particle size is 300～400 μm) of 40wt.%, continues mix homogeneously, finally
The powder pressing forming that will mix, obtains green compact, press power 100MPa, press temperature 30 DEG C, compacting
10 minutes time；
(2) green compact that (1st) step suppresses are put in vacuum high temperature furnace, be first evacuated to 0.01Pa
Hereinafter, and it is always maintained at vacuum, then carries out presintering at 200 DEG C of insulation 2h and remove ammonium hydrogen carbonate,
Obtain porous green compact；
(3) then in identical vacuum drying oven, (2) acquisition porous green compact are filled with argon to be sintered, argon
Air pressure is 820Pa, sintering temperature 1150 DEG C, sintering time 10h, after having sintered, and sample furnace cooling
To room temperature, obtain the high-strength light high-ductility NiTi marmem composite damping that the second phase is compound with hole
Material.
Measure this example preparing the porosity of sample by relative density method is 60%, and Figure 16 is the gold of this sample
Phase photo, the hole of this sample is double size distributions, a kind of macropore being about about 400 μm and another kind
The aperture of 50 100 μm.The phase transition temperature of this sample is: Mf=40 DEG C, Ms=73 DEG C, As=75 DEG C, Af=108
DEG C, still it is mainly NiTi martensite and Ti under this sample room temperature2Ni phase, shines from high power and low power scanning electron microscope
Sheet sees (a) and (b) in Figure 17 it can be seen that size is at the Ti of 2～3 μm2Ni phase even dispersion ground point
Cloth is on NiTi phase matrix.The room temperature compression failure curve of this sample as shown in figure 18, in the high hole of 60%
Under gap rate, compressed rupture strength is still up to 76.5MPa, and its breaking strain most important is up to 25.2%,
The NiTi memorial alloy being much better than under same porosity.The sample of this pair of yardstick height hole shows excellent
Damping capacity, it damps temperature curve continuously and sees Figure 19, when strain amplitude is 1%, high temperature austenite state
Damped coefficient is up to 0.06；The damping of low-temperature martensite state is more excellent, is more up to 0.075.
Above-described embodiment is the present invention preferably embodiment, but embodiments of the present invention are not by described reality
Execute the restriction of example, the change made under other any spirit without departing from the present invention and principle, modification,
Substitute, combine, simplify, all should be the substitute mode of equivalence, within being included in protection scope of the present invention.
Claims (10)
1. the preparation method of wide temperature range high-strength light high-ductility NiTi marmem composite damping material, its
It is characterised by comprising the following steps:
(1) mixed powder: pure nickel powder and pure titanium valve are pressed atomic ratio (100 x): x mix homogeneously, x is 52～64；
The powder pressing forming that will mix, obtains green compact；
(2) sintering: the green compact that step (1) suppresses are put in high temperature furnace, is first evacuated to 0.01Pa
Hereinafter, being filled with protective gas and carry out protection sintering, controlling sintering temperature is 1000～1200 DEG C, sintering time
Being 5～20 hours, after having sintered, product cools to room temperature with the furnace, obtains the second phase and hole compound
High-strength light high-ductility NiTi marmem composite damping material.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1
The preparation method of damping material, it is characterised in that: the purity more than 99.5% of described pure titanium valve, particle size
50～75 μm；The purity more than 99.5% of described pure nickel powder, particle size is 50～75 μm.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1
The preparation method of damping material, it is characterised in that: step (1) described mixing is to use ball-milling method or conventional mixed
Powder method mixes.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1
The preparation method of damping material, it is characterised in that: step (1) described compressing be use die pressing carry out；
Described compressing pressure is 50～600MPa, and temperature is 30～100 DEG C, time 3～15 minutes.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1
The preparation method of damping material, it is characterised in that: step (1) green compact also include pore creating material；Pore creating material adds
Enter mode be pure nickel powder and pure titanium valve by atomic ratio (100 x): include after x mix homogeneously adding pore creating material,
Pore creating material is mixed homogeneously with NiTi mixed powder, or pure nickel powder and pure titanium valve and pore creating material mix homogeneously；
The powder pressing forming that will mix, obtains green compact；Described pore creating material is ammonium hydrogencarbonate or carbamide, purity
More than 99%, particle size 100～500 μm；The addition of pore creating material is NiTi mixed powder quality
0～50%；Addition pore creating material and the green compact suppressed are put in high temperature furnace, are first evacuated to below 0.01Pa,
And it is always maintained at vacuum, then carry out presintering except pore creating material, it is thus achieved that porous green compact re-sinter.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 5
The preparation method of damping material, it is characterised in that: described pre-sintering temperature 200 250 DEG C, the presintering time is
0.1～5 hour.
A kind of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1 is multiple
Close the preparation method of damping material, it is characterised in that: described high temperature furnace is low-pressure sintering furnace or electron tubes type
Stove.
The compound resistance of wide temperature range high-strength light high-ductility NiTi marmem the most according to claim 1
The preparation method of damping material, it is characterised in that: described protective gas is argon；The air pressure of protective gas is
300Pa～4MPa.
9. a wide temperature range high-strength light high-ductility NiTi marmem composite damping material, its feature exists
Prepare by preparation method described in any one of claim 1～8 in it；Material is strong in the compression of 100 DEG C～200 DEG C
Degree is 76～1620MPa, and compressible strain is 10～32%, and damped coefficient is 0.025～0.08；Material has
10～the porosity of 60% and the hole of 100～500 μm, the density of material is less than 5g/cm3。
10. wide temperature range high-strength light high-ductility NiTi marmem composite damping material described in claim 9
Expect as automobile or spaceborne energy-absorbing and the application of protecting against shock parts, or as tank or the suction of submarine
Sound, vibration isolation and the application of protecting against shock material.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109112362A (en) * | 2018-08-30 | 2019-01-01 | 中南大学 | A kind of dedicated substrate of Ti-Ni marmem and preparation method thereof of 4D printing flawless |
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| CN115261656A (en) * | 2022-06-21 | 2022-11-01 | 中南大学 | Preparation method of low-cost element mixed porous NiTi shape memory alloy through vacuum high-temperature sintering and aging treatment |
| CN115961166A (en) * | 2022-11-21 | 2023-04-14 | 四川大学 | By using Ti 2 Ni、TiNi 3 Method for preparing TiNi alloy from intermediate alloy |
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| Publication number | Priority date | Publication date | Assignee | Title |
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1131701A (en) * | 1995-03-22 | 1996-09-25 | 中国科学院金属研究所 | Foam nickel titanium memory alloy |
| US20070123976A1 (en) * | 2005-09-23 | 2007-05-31 | Bin Yuan | Pseudoelastic porous shape memory materials for biomedical and engineering applications |
| CN101709399A (en) * | 2009-11-30 | 2010-05-19 | 华南理工大学 | Surface modification method for porous NiTi shape memory alloy |
| CN101818277A (en) * | 2010-01-29 | 2010-09-01 | 华南理工大学 | Method for preparing super-elastic gradient-porosity porous NiTi alloy |
| CN102534275A (en) * | 2012-01-09 | 2012-07-04 | 华南理工大学 | TiNi alloy-based composite material with near-zero thermal expansion characteristic and preparation method thereof |
| CN103060589A (en) * | 2012-12-20 | 2013-04-24 | 华南理工大学 | Preparation method of gradient nickel (Ni) titanium (Ti) shape-memory alloy with multiple pores |
| CN104152738A (en) * | 2014-08-14 | 2014-11-19 | 昆明理工大学 | Method for manufacturing biomedical porous nickel titanium alloy |
-
2016
- 2016-06-16 CN CN201610436782.2A patent/CN105908000B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1131701A (en) * | 1995-03-22 | 1996-09-25 | 中国科学院金属研究所 | Foam nickel titanium memory alloy |
| US20070123976A1 (en) * | 2005-09-23 | 2007-05-31 | Bin Yuan | Pseudoelastic porous shape memory materials for biomedical and engineering applications |
| CN101709399A (en) * | 2009-11-30 | 2010-05-19 | 华南理工大学 | Surface modification method for porous NiTi shape memory alloy |
| CN101818277A (en) * | 2010-01-29 | 2010-09-01 | 华南理工大学 | Method for preparing super-elastic gradient-porosity porous NiTi alloy |
| CN102534275A (en) * | 2012-01-09 | 2012-07-04 | 华南理工大学 | TiNi alloy-based composite material with near-zero thermal expansion characteristic and preparation method thereof |
| CN103060589A (en) * | 2012-12-20 | 2013-04-24 | 华南理工大学 | Preparation method of gradient nickel (Ni) titanium (Ti) shape-memory alloy with multiple pores |
| CN104152738A (en) * | 2014-08-14 | 2014-11-19 | 昆明理工大学 | Method for manufacturing biomedical porous nickel titanium alloy |
Non-Patent Citations (3)
| Title |
|---|
| D.S. LI等: "High porosity and high-strength porous NiTi shape memory alloys with controllable pore characteristics", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
| M.LGHARO等: "Ti-Ni形状记忆合金的压制和烧结行为", 《稀有金属材料与工程》 * |
| 马旭梁等: "多孔NiTi形状记忆合金的制备及性能", 《材料工程》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109112362A (en) * | 2018-08-30 | 2019-01-01 | 中南大学 | A kind of dedicated substrate of Ti-Ni marmem and preparation method thereof of 4D printing flawless |
| CN109112362B (en) * | 2018-08-30 | 2020-08-04 | 中南大学 | Special substrate for 4D printing of crack-free titanium-nickel shape memory alloy and preparation method thereof |
| WO2023109507A1 (en) * | 2021-12-17 | 2023-06-22 | 华南理工大学 | Shape memory alloy screen pipe material with ultrahigh strain recovery, and preparation method therefor and application thereof |
| CN114875265A (en) * | 2022-04-07 | 2022-08-09 | 华南理工大学 | Wide-temperature-range light NiTiSi shape memory alloy damping material and preparation method and application thereof |
| CN115261656A (en) * | 2022-06-21 | 2022-11-01 | 中南大学 | Preparation method of low-cost element mixed porous NiTi shape memory alloy through vacuum high-temperature sintering and aging treatment |
| CN115961166A (en) * | 2022-11-21 | 2023-04-14 | 四川大学 | By using Ti 2 Ni、TiNi 3 Method for preparing TiNi alloy from intermediate alloy |
| CN115961166B (en) * | 2022-11-21 | 2024-05-17 | 四川大学 | By Ti2Ni、TiNi3Method for preparing TiNi alloy by using intermediate alloy |
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