CN1081242C - Process for preparing TiNi-base marmem directly from elements powder - Google Patents
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Abstract
The present invention relates to a processing method for metal powder. In the method, raw material powder of Ti powder, Ni powder, etc. are evenly blended and are made into blanks by cold isostatic compaction; the blanks are treated by vacuum packaging with glass or metal and embedded into composite material fluid moulds to be made into blanks for pressing; the blanks are treated by heat-agglomerating for 0.5 to 2 hours at the temperature of 750 to 1, 050 DEG C and then pressed for 5 to 60 seconds under the pressure of 300 to 1, 000MPa to remove cladding materials such as glass fluid moulds, etc. and obtain TiNi base alloy ingots. The processing method has the advantages of simple process and apparatus, high material utilization rate and low cost.
Description
The present invention relates to the working method of metal-powder, prepare the method for TiNi base marmem more precisely with reaction sintering and quick omnidirectional.
The research and development of novel material is one of present countries in the world competition focal point.The TiNi shape memory alloy is the best shape memory alloys of various so far over-all propertieies, has extensive and important purposes.It is widely used in fields such as Aeronautics and Astronautics, machinery, intelligent material technology, medical science, agriculturals at present, becomes a kind of important new function material.
Current, industrial main employing vacuum consumable arc-melting or vacuum induction melting are refined the TiNi shape memory alloy.This method can obtain fine and close TiNi alloy.Material composition was difficult to accurate control when the weak point of this method was melting, thereby made the phase change temperature of shape memory alloy also be difficult to control.This is because the transformation temperature of TiNi alloy alters a great deal along with the difference of chemical ingredients.For example 0.1% Ni content deviation can cause transformation temperature M
sThe variation of 10K appears.Use vacuum consumable electrode arc furnace to carry out melting, because of charging feedstock can not melt simultaneously, it is very difficult obtaining there is not the uniform ingot casting of composition of segregation, thereby needs repeatedly melting.Simultaneously,, be subject to the pollution of impurity such as carbon, nitrogen, oxygen during melting, materials processing performance and use properties are worsened because titanium fusing point height is active strong.So when melting,, melting atmosphere and environment are wanted strict control, to avoid the generation of various inclusiones to the material of crucible.And many pores and defective are arranged with vacuum consumable arc-melting or vacuum induction melting resulting TiNi ingot casting surface and top, these pores and defective can cause the cracking of material when hot-work, therefore before hot-work, to strip off the skin, crop, add the loss of actual in-process stock, the material recovery rate of TiNi alloy has only 30～40%, cause its production cost height, limited it and applied.Therefore, explore low cost, high performance Ti Ni alloy technology of preparing becomes urgent problem in the shape memory alloy technical development.
Powder metallurgic method also is the method for preparing the TiNi shape memory alloy.It is to be raw material with Ti powder, Ni powder, through thorough mixing aftershaping sintering, preparation TiNi alloy, but problem is to be difficult to obtain densification and the TiNi alloy of sufficient reacting, simultaneously having brought a shortcoming again, is exactly that oxygen level strengthens, and so not only causes the change of TiNi alloying constituent, and its mechanical property is significantly worsened, and the sintering period is long.
In order to overcome the deficiency of powder metallurgic method, the method for the another kind of TiNi of preparation alloy has been proposed, it is that the thick Ti powder of employing is a raw material, carries out densification with hot isostatic pressing (Hot Isostatic Pressing is called for short HIP).Concrete method is at first raw material Ti powder and Ni powder to be mixed, and mixes the powder moulding, and through 1000 ℃, 10 hours sintering obtains single-phase TiNi alloy, jacket then, and through 950 ℃, 1 hour hot isostatic pressing elimination intrinsic space.The billet that obtains in this way can through subsequently be processed into TiNi plate or wire rod.This method weak point is that operation is many, and the time is long, the requirement height of raw material powder, and used hot isostatic pressing, cost up.
SHS (Self-propagating High-temperature Systhesis is called for short SHS) is when forming compound, a kind of new technology of utilizing the generation heat between element to synthesize material requested.Japan metallic substance institute has proposed to utilize SHS to prepare the method for TiNi alloy.This method is that a certain proportion of titanium valve, nickel powder fully are mixed, with isostatic cool pressing (Cold Isostatic Pressing, abbreviation CIP) forming TiNi alloy relative density is 50-60%, again with the synthetic TiNi intermetallic compound of SHS method, use HIP fixed then, make relative density and reach 100% billet.The TiNi alloy of this billet can forge under 1000 ℃, and extruding, thermoplasticity such as rolling are processed into various wire rods and sheet material.The process characteristic of this method is the transition temperature that can control the TiNi alloy exactly, under the prerequisite of control powder quality, can obtain the lower billet of oxygen level, and because billet does not have the segregation of chemical ingredients, the cold and hot working performance of gained material and end article performance are all good relatively, but also used the HIP technology, the cost height, operation is long.
Fast omnidirectional's compacting (Rapid Omnidirectional Compaction is called for short ROC) is the new technology of a kind of development in recent years powdered material density of getting up.Be that a kind of fluid that utilizes produces static pressure as transmission medium, powder compression helped the quasi-hot isostatic pressing technology of dense product.It is compared with hot isostatic pressing, and the compacting of quick omnidirectional has advantages such as production cost is low, and the structure property of treated material is better.
Purpose of the present invention just is to work out a kind of novel method that is directly prepared the TiNi shape memory alloy by element powders.Attempt that the reaction sintering (Reactive sintering) of powder is suppressed (ROC) two technologies with quick omnidirectional and combine (novel process that forms is called for short RROC like this), be raw material directly by element powders, one step obtained sufficient reacting and complete closely knit TiNi shape memory alloy technology, formed the method that a kind of low cost prepares the TiNi base marmem.
In fact, method of the present invention is exactly that the reaction sintering of TiNi and ROC densification are integrated, and promptly carries out reacting between element powders synthetic in the ROC heating phase, finishes end reaction and densification process by ROC at last.
The present invention is a kind of method that is directly prepared the TiNi base marmem by element powders, at first with the raw material powder mixing, become blank with cold isostatic compaction, the relative density that makes blank is 55-80%, said raw material powder is the Ti powder, the Ni powder, the Ti powder accounts for 48～51 atomic percents, the Ni powder accounts for 49～52 atomic percents, the mean particle size of all raw material powder 〉=20 μ m～＜149 μ m, after blank carried out vacuum canning with glass or metal, and imbed to make in the fluid mould and suppress with base (being called ROC compacting base), under 750-1050 ℃ temperature, carry out heat-agglomerating 0.5-2 hour (being called the ROC heating), in heat-processed, carry out the reaction sintering between raw material powder, make it become TiNi base alloy substantially, the compacting that basically forms TiNi base alloy is carried out pressure 300-1000MPa with base, the compacting of time 5-60 second (being called the ROC compacting), in the ROC pressing process, further finish the transformation of raw material powder to TiNi base alloy, and reach closely knit fully, remove glass or metal, coating materials such as fluid mould obtain TiNi base alloy billet.
When using isostatic cool pressing, the relative density that makes blank is that 55-80% is good.
Used raw material powder is titanium (Ti) powder, nickel (Ni) powder, and the Ti powder accounts for 48～51 atomic percents, and the Ni powder is 49～52 atomic percents.
In TiNi base alloy, add the third element and can obviously improve its performance, to satisfy different needs as raw material powder.The third element raw material powder that is added is that Cu, Cr, Fe, Nb, Co, Mn a kind of elemental metalpowder wherein substitutes nickel powder or titanium valve.The amount of the metallic element copper powder that is added is 0.1～30 atomic percent, and the Nb powder is 0.1～12 atomic percent, and the amount of the elemental metalpowder that Cr, Fe, Co, Mn are wherein a kind of is 0.1～10 atomic percent.Add above-mentioned elemental metalpowder and can form unique TiNi base memorial alloy.Be applied the shape memory alloy of excellent property of the TiNiCu shape memory alloy that the copper elemental metalpowder that adds replaces nickel to form.Studies show that adding the Cu elemental metalpowder has the stable phase height, reduces the hysteresis of phase transformation, improves alloy property, especially effect such as restorability.From the powder metallurgy angle, the Cu powder is than Ni powder considerably cheaper, and raw materials cost obviously will reduce; Consider from manufacture technology simultaneously,, increase the Cu powder and do not increase how many workloads because mixed powder process is arranged equally.It is more even tiny to obtain alloy organizing with powder method simultaneously, helps later processing and uses.
Above-mentioned raw material powder total impurities content is less than 0.5% weight percentage, and wherein carbon content is less than 0.25% weight percentage, and oxygen level is less than 0.25% weight percentage.(annotate 400 orders is equivalent to～0.037mm the mean particle size of all former powder in the scope of 〉=20 μ m～＜149 μ m, 300 orders are equivalent to-0.044mm, 100 orders are equivalent to-and 0.149mm), the mean particle size of all raw material powder is (100～400 order) well in the scope of 〉=37 μ m～＜149 μ m.
Making after compacting imbeds the fluid mould with base (be called ROC suppress use base), carry out heat-agglomerating.When determining to carry out the temperature of heat-agglomerating,, can not generate the TiNi alloy, about 950 ℃, Ti occur at (below 630 ℃) under the lower temperature with reference to the Ti-Ni phasor
2The liquid phase of Ni, the reaction between powder will aggravate greatly, then occurring a large amount of liquid phases more than 1120 ℃, near melting condition.Consider Temperature Influence, under 750-1050 ℃ temperature, carried out heat-agglomerating 0.5-2 hour.Again under 950-1050 ℃ temperature, to carry out heat-agglomerating 0.5-2 hour for good.Fig. 1 a and Fig. 1 b are that the time of carrying out heat-agglomerating is 45 minutes, and the situation of product metallographic structure under the differential responses sintering temperature cooperates the scan-probe analysis as can be known, and product quite major part is the TiNi phase, and tangible TiNi is arranged in the time of 980 ℃
3Phase then is difficult to find TiNi in the time of 1020 ℃
3Phase comes to the same thing with X light diffracting analysis.The temperature of carrying out heat-agglomerating of Fig. 1 a is 980 ℃; The heat-agglomerating temperature of carrying out of Fig. 1 b is 1020 ℃.
Fig. 2 a and the situation (not eroded) of Fig. 2 b for the product metallographic of different time of sintering when carrying out sintering for 980 ℃.Fig. 2 a is for to add thermojunction 15 minutes in 980 ℃; Fig. 2 b is for to carry out heat-agglomerating 45 minutes in 980 ℃.As seen under short situation of sintering reaction time, there is tangible uneven components tissue from Fig. 2 a in the product, is mainly the TiNi of rich nickel
3Deng intermediate product (bulk stain among the figure), and under the situation of long reaction time, above-mentioned heterogeneous structure fades away, and becomes single TiNi tissue.
With compacting with base basically form TiNi base alloy, when carrying out the ROC compacting and pressurizeing, as shown in Figure 3, product density and pressing pressure are the index corresponding relation, and promptly with the raising of pressure, its density increases rapidly, after to a certain degree, rate of growth is slack-off, reaches fully dense 100% density very soon.Test shows, just can reach 100% density under the pressure of 500MPa.Fig. 4 a, Fig. 4 b demonstrate the microtexture of products therefrom under the different pressures.By among Fig. 4 a as seen, under the 300MPa condition, be distributed with very a spot of micro-pore (stain among the figure), along with the rising hole of pressure obviously reduces, the result forms corresponding relation with density analysis.
With respect to HIP technology, the employed pressure of ROC process is quite high, and material reaches closely knit in moment, so the employed dwell time of ROC comparatively speaking can be quite short, the influence of dwell time to density is shown in Table 1.When pressure ratio was higher, the short period of time just can reach fine and close effect, and the dwell time does not almost change from 5～45 seconds product density.Certainly the longer time of pressurize, still the oversize time has not had any necessity.But, when pressure is low relatively, the densification of depended on pressure relatively a little less than, at this moment prolong the dwell time and be equivalent to prolong the pyroreaction time, help improving densification degree to a certain extent.So, with compacting with base basically form TiNi base alloy, carry out pressure 300-1000MPa, the compacting (being called ROC suppresses) of time 5-60 second, again carrying out pressure 450-1000MPa, being compressed to of time 5-30 second.
The relation of table 1 density and dwell time
| Time (S) | 5 | 20 | 45 |
| Pressure (300MPa) | 6.43 | 6.44 | 6.44 |
| Pressure (1000MPa) | 6.44 | 6.45 | 6.45 |
Annotate: the 6.45th, the theoretical density of TiNi alloy
Carry out vacuum canning with glass or metal, oxidation when preventing the raw material powder reacting by heating, used glass is borate glass, silicate glass a kind of glass wherein.Used metal is copper or the good steel of plasticity.
Said fluid mould be the composite material stream phantom as shown in Figure 5, it is made of dispersive flowable glass particle and successive heat-stable ceramic skeleton under Heating temperature.When heating and moving, heat-resisting skeleton has guaranteed the globality of fluid mould; Under the situation of compacting, heat-resisting skeleton fragmentation is with hydrostatic pressure such as glass flow produce.This fluid is molded, and to do cost low, and sealing is simple, removes easily, and employed temperature can be from 315 ℃ to 1650 ℃.
At first will carry out blank behind the vacuum canning with glass or metal and be embedded in and constitute fluid module zoarium in the fluid mould, molectron heats in common electric furnace, under 750～1050 ℃ temperature, carries out heat-agglomerating 0.5-2 hour.The fit immigration of fluid module after the heating carried out the ROC compacting in the pressing mold tool.Then, fluid module zoarium is pushed out, and obtains product by beaing removal fluid mould.The synoptic diagram of ROC method is seen Fig. 6.
The ROC process unit of the instantaneous generation hot isostatic pressing of energy effect is the basic equipment of whole work, and the ROC process unit must guarantee to bear the combined action of High Temperature High Pressure.A whole set of ROC process unit is installed on the vertical four-column type oil press, and ROC device synoptic diagram is seen shown in Figure 7.The centre portions of device is the pressure-bearing mould.In order to guarantee that temperature is fallen to such an extent that be not too fast (guaranteeing the hot isostatic pressing effect of fluid mould) in pressing process, the well heater of outside carries out the preheating of pressure-bearing mould.The pressure-bearing mould is made up of urceolus, middle tube, inner core.The temperature of pressure-bearing mould detects by inserting the intravital thermopair of tube, and uses DW902 type temperature controller to carry out temperature control.Temperature is controlled at 400-500 ℃.Oil press is used to produce required axial pressing force of ROC when compacting, carries out pressure 300-1000MPa, the compacting (being called the ROC compacting) of time 5-60 second.
The pressure-bearing mould is the key part that bears High Temperature High Pressure, and the ROC operating pressure of method of the present invention is 300～1000MPa.This pressure belongs to the ultra-high voltage scope, and very tight for the requirement of pressure-bearing mould, the pressure-bearing mould adopts three layers of tube structure of shrink-on for this reason.
The advantage that directly prepares TiNi base marmem method by element powders of the present invention just is:
1. method of the present invention has overcome shortcomings such as prior powder metallurgy method material is not fine and close, can reduce production costs effectively again, thereby has formed a kind of novel method of the TiNi of preparation base marmem.Technology, equipment are simple.
2. the TiNi base marmem relative density that obtains by method of the present invention can reach 100%, and crystal grain is fine and closely woven, and uniform ingredients is functional, can keep blank shape, can directly make device uses such as tube stub; Also can make sheet material through following process such as extruding, rolling, drawings, wire rod uses; Directly make part, material use efficiency is greater than 90%, and following process is used, and material use efficiency is greater than 80%.
3. the heating of method of the present invention and pressing process all can be used common process furnace and pressing machine, and can be with forged productivity production, thereby have reduced the production cost of TiNi base marmem.
Fig. 1 a, Fig. 1 b are heat-agglomerating product tissue (* 200) under the differing temps
Fig. 1 a is 980 ℃, and Fig. 1 b is 1020 ℃.The test conditions of Fig. 1 a, Fig. 1 b is Ti-50 atomic percent Ni, the base density 65% of colding pressing, and the heat-agglomerating time is 45 minutes, ROC pressure 1000MPa, the dwell time is 20 seconds.
Fig. 2 a, Fig. 2 b are different time heat-agglomerating product metallographic sheet (* 100)
Fig. 2 a is heat-agglomerating 15 minutes, and Fig. 2 b is heat-agglomerating 45 minutes.The test conditions of Fig. 2 a, Fig. 2 b is Ti-50 atomic percent Ni, and the base density 65% of colding pressing, heat-agglomerating temperature are 980 ℃, ROC pressure 1000MPa, 20 seconds dwell times.
Fig. 3 density is with ROC pressing pressure changing conditions
Among the figure, ordinate zou is density (g/cm
3), X-coordinate is pressure (MPa).Test conditions is 980 ℃ for the heat-agglomerating temperature, and the heat-agglomerating time is 45min, alloying constituent Ti-50 atomic percent Ni, the base density 65% of colding pressing, 20 seconds dwell times.
Fig. 4 a, Fig. 4 b are microstructure of product under the different pressures (* 100)
Fig. 4 a is 300MPa, and Fig. 4 b is 1000MPa.Test conditions is 980 ℃ for the heat-agglomerating temperature, heat-agglomerating time 45min, alloying constituent Ti-50 atomic percent Ni, the base density 65% of colding pressing, 20 seconds dwell times.
Fig. 5 composite material stream phantom is formed
Among the figure, 1 is glass particle moving phase, and 2 is heat-resisting skeleton.
Fig. 6 ROC method synoptic diagram
Among the figure, 3 is drift, and 4 is mould, and 5 is raw material powder, and 6 is the pre-heated flow phantom, and 7 is the fluid mould, and 8 is the product of 100% density.
Fig. 7 ROC device synoptic diagram
Among the figure, 9 is the well heater of outside, and 10 is thermal insulation layer, and 11 is middle tube, and 12 is inner core, and 13 is urceolus, and 14 is thermometer hole, and 15 is pressure-bearing mould mould.
Below with embodiment method of the present invention is further described, will help to do further to understand for method of the present invention and advantage thereof, protection scope of the present invention is not subjected to the restriction of these embodiment, protection scope of the present invention is decided by claim.
Embodiment 1
Raw material Ti powder, Ni powder are mixed it with ball milled in the ratio of 49.6 atomic percent Ti-50.4 atomic percent Ni, contain Ti 99.5% weight percentage in the Ti powder, the mean particle size of Ti powder is 20 μ m, carbon content is＜0.2% weight percentage in the Ti powder, oxygen level is＜0.25% weight percentage in the Ti powder, contain Ni 99.8% weight percentage in the Ni powder, the Ni powder is that mean particle size is 45 μ m.Become blank with cold isostatic compaction, making its relative density is 75%, carry out vacuum canning with borate glass or silicate glass, and imbed and make the compacting base in the composite material stream phantom, heating was carried out reaction sintering 0.75 hour under 1020 ℃ temperature in common electric furnace, made it become TiNi base alloy substantially.To carry out the compacting base that basically forms TiNi base alloy of heat-agglomerating reaction, under the pressure of 1000MPa, carry out 25 seconds compacting (being called the ROC compacting), the temperature of pressure-bearing mould is 450 ℃, further finishes the transformation of raw material powder to TiNi base alloy in the ROC pressing process, and reaches closely knit fully, remove coating materials such as glass, fluid mould, obtain TiNi base alloy billet, the overwhelming majority becomes the TiNi alloy in the product, has only minute quantity TiNi
3, mean grain size 30 μ m, density is 6.45g/cm
3
Its working method and processing condition are substantially with embodiment 1, only different is with the ratio of raw material powder in 50 atomic percent Ti-30 atomic percent Ni-20 atomic percent Cu, with ball milled it to be mixed, contain Cu 99.7% in the Cu powder, mean particle size is 25 μ m.Become blank with cold isostatic compaction, making its relative density is 70%, carries out reaction sintering 1.17 hours under 950 ℃ temperature, under the pressure of 700MPa, carries out 20 seconds ROC compacting.The overwhelming majority is the TiNiCu alloy in the product, has only minute quantity Ti
2Cu, mean grain size 70 μ m, density 6.38g/cm
3
Its working method and processing condition are substantially with embodiment 1, and only different is that the ratio of raw material powder in 50 atomic percent Ti-45 atomic percent Ni-5 atomic percent Cu mixed it with ball milled, contains Cu 99.7% in the Cu powder, and mean particle size is 25 μ m.Become blank with cold isostatic compaction, making its relative density is 80%, carries out reaction sintering 1.5 hours under 980 ℃ temperature, carries out 30 seconds compacting of pressurize under the pressure of 500MPa, and the product overwhelming majority is the TiNiCu alloy, has only minute quantity Ti
2Cu, mean grain size 80 μ m, density 6.44g/cm
3
Its working method and processing condition are substantially with embodiment 1, only different is that the ratio of raw material powder in 45 atomic percent Ti-45 atomic percent Ni-10 atomic percent Cu mixed it with ball milled, contain Cu 99.7% in the Cu powder, mean particle size is 25 μ m.Become blank with cold isostatic compaction, making its relative density is 75%, carries out reaction sintering 1 hour under 1000 ℃ temperature, carries out 20 seconds compacting of pressurize under the pressure of 1000MPa, and the product overwhelming majority is the TiNiCu alloy, has only minute quantity Ti
2Cu, mean grain size 50 μ m, density 6.45g/cm
3
Test shows that Cu content not only can improve some key property of alloy in a word, can also reduce the cost of alloy, owing to high temperature in the fusion process slowly cools off the Ti that separates out and be enriched on the crystal boundary down
2Cu has had a strong impact on the processing characteristics of TiNiCu alloy, Cu content among the TiNiCu that smelting process is produced is difficult for surpassing 7%, use the TiNiCu alloy of method preparation of the present invention, preparation temperature is low relatively, improvement for processing characteristics has vital role, therefore utilize this law, can obtain higher Cu content on the one hand, and can improve the processing characteristics of TiNiCu alloy.
Its working method and processing condition are substantially with embodiment 1, only different is that the ratio of raw material powder in 50 atomic percent Ti-50 atomic percent Ni mixed it with ball milled, titaniferous 99.8% weight percentage in the Ti powder, the mean particle size of Ti powder are 70 μ m.Become blank with cold isostatic compaction, making its relative density is 55%, carries out reaction sintering 0.5 hour under 1040 ℃ temperature, carries out 45 seconds compacting of pressurize under the pressure of 1000MPa, obtains qualified product.
Its working method and processing condition are substantially with embodiment 1, only different is that the ratio of raw material powder in 50 atomic percent Ti-50 atomic percent Ni mixed it with ball milled, become blank with cold isostatic compaction, making its relative density is 80%, under 750 ℃ temperature, carried out reaction sintering 2 hours, under the pressure of 350MPa, carry out pressurize 60 seconds, obtain qualified product.
Claims (9)
1. one kind directly prepares the method for TiNi base marmem by element powders, it is characterized in that,
1) at first with the raw material powder mixing, become blank with cold isostatic compaction, the relative density that makes blank is 55-80%, and said raw material powder is the Ti powder, the Ni powder, the Ti powder accounts for 48～51 atomic percents, the Ni powder accounts for 49～52 atomic percents, the mean particle size of all raw material powder 〉=20 μ m～＜149 μ m, blank carried out vacuum canning with glass or metal after, and imbed and make the compacting base in the fluid mould
2) under 750-1050 ℃ temperature, carried out heat-agglomerating 0.5-2 hour, make it become TiNi base alloy substantially,
3) will basically form the compacting base of TiNi base alloy, carry out pressure 300-1000MPa, the compacting of time 5-60 second, and reach closely knit fully,
4) remove glass or metal, fluid mould coating material, obtain TiNi base alloy billet.
2. according to a kind of method that directly prepares the TiNi base marmem by element powders of claim 1, it is characterized in that, add the third element as raw material in TiNi base alloy, the third element raw material powder that is added is that Cu, Cr, Fe, Nb, Co, Mn a kind of elemental metalpowder wherein substitutes nickel powder or titanium valve.
3. directly prepare the method for TiNi base marmem according to a kind of of claim 2 by element powders, it is characterized in that the amount of metallic element Cu powder is 0.1～30 atomic percent.
4. directly prepare the method for TiNi base marmem according to a kind of of claim 2 by element powders, it is characterized in that the amount of Nb powder is 0.1～12 atomic percent.
5. directly prepare the method for TiNi base marmem according to a kind of of claim 2 by element powders, it is characterized in that the amount of the elemental metalpowder that Cr, Fe, Co, Mn are wherein a kind of is 0.1～10 atomic percent.
6. according to a kind of method that directly prepares the TiNi base marmem by element powders of claim 1, it is characterized in that, raw material powder total impurities content is less than 0.5% weight percentage, and wherein carbon content is less than 0.25% weight percentage, and oxygen level is less than 0.25% weight percentage.
7. directly prepare the method for TiNi base marmem according to a kind of of claim 1 by element powders, it is characterized in that the mean particle size of raw material powder 〉=37 μ m～＜149 μ m.
8. directly prepare the method for TiNi base marmem according to a kind of of claim 1 by element powders, it is characterized in that, under 950-1050 ℃ temperature, carried out heat-agglomerating 0.5-2 hour.
9. directly prepare the method for TiNi base marmem according to a kind of of claim 1 by element powders, it is characterized in that, carry out pressure 450-1000MPa, the compacting of time 5-30 second.
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| CN1218814C (en) * | 2003-12-15 | 2005-09-14 | 高峻峰 | Method for manufacturing metal or ceramic bond superhard grinding tool |
| CN104630525A (en) * | 2015-01-29 | 2015-05-20 | 华南理工大学 | Porous NiTiNb superelastic alloy with low strain hysteresis and preparation method of alloy |
| CN105907998A (en) * | 2016-05-06 | 2016-08-31 | 陈昌 | Porous metal material and preparation method thereof |
| CN106191624A (en) * | 2016-07-08 | 2016-12-07 | 江苏科技大学 | A kind of marmem and its preparation method and application |
| CN108296480B (en) * | 2018-03-23 | 2020-01-31 | 厦门理工学院 | Preparation method of high-purity refractory metal blocks |
| CN111151756B (en) * | 2020-01-20 | 2021-12-03 | 广东省科学院新材料研究所 | 4D printing rapid manufacturing method of shape memory alloy pipe joint and product |
| CN112342439A (en) * | 2020-10-21 | 2021-02-09 | 江西省科学院应用物理研究所 | High-thermal-stability nanocrystalline NiTi-W composite material and preparation method thereof |
| CN115029585A (en) * | 2022-05-27 | 2022-09-09 | 中国航发四川燃气涡轮研究院 | NiTiCu alloy material and preparation method thereof, spray pipe and additive manufacturing method thereof |
| CN114875294B (en) * | 2022-06-07 | 2023-05-12 | 上海工程技术大学 | Titanium nickel base alloy material and preparation method and application thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1131701A (en) * | 1995-03-22 | 1996-09-25 | 中国科学院金属研究所 | Foam nickel titanium memory alloy |
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| 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 |
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