CN1403611A - Mechanical training method for Ti-Ni marmem - Google Patents
Mechanical training method for Ti-Ni marmem Download PDFInfo
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- CN1403611A CN1403611A CN 01128129 CN01128129A CN1403611A CN 1403611 A CN1403611 A CN 1403611A CN 01128129 CN01128129 CN 01128129 CN 01128129 A CN01128129 A CN 01128129A CN 1403611 A CN1403611 A CN 1403611A
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- marmem
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- mechanical training
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- 229910004337 Ti-Ni Inorganic materials 0.000 title claims abstract description 18
- 229910011209 Ti—Ni Inorganic materials 0.000 title claims abstract description 18
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 title claims abstract description 18
- 238000000034 method Methods 0.000 title claims abstract description 15
- 239000000463 material Substances 0.000 claims abstract description 17
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 14
- 229920006395 saturated elastomer Polymers 0.000 claims abstract description 5
- 239000000956 alloy Substances 0.000 claims description 15
- 229910045601 alloy Inorganic materials 0.000 claims description 12
- 230000009466 transformation Effects 0.000 claims description 10
- 230000035882 stress Effects 0.000 claims description 9
- 230000032683 aging Effects 0.000 claims description 7
- 230000006835 compression Effects 0.000 claims description 7
- 238000007906 compression Methods 0.000 claims description 7
- 238000000137 annealing Methods 0.000 claims description 5
- 238000009792 diffusion process Methods 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 4
- 239000004744 fabric Substances 0.000 claims description 4
- 239000006104 solid solution Substances 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 239000000243 solution Substances 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 2
- 229910001285 shape-memory alloy Inorganic materials 0.000 abstract description 10
- 230000008859 change Effects 0.000 abstract description 3
- 230000007704 transition Effects 0.000 description 3
- 230000008901 benefit Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000003446 memory effect Effects 0.000 description 2
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910010380 TiNi Inorganic materials 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 230000000875 corresponding effect Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000008447 perception Effects 0.000 description 1
- 230000008569 process Effects 0.000 description 1
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Abstract
The present invention relates to shape memory alloy, and is especially the mechanical training method for Ti-Ni shape memory alloy. By means of stress control or strain control mode and through symmetrical pulling and pressing to load to reach the saturated circulation stress times at room temperature. Ti-Ni shape memory alloy with stable martensite phase change temperature is obtained. The present invention has short training time and no damage to the material, can save power and lower training cost, and is suitable for industrial application.
Description
Technical field
The present invention relates to shape memory alloy, be specially a kind of mechanical training method for Ti-Ni marmem.
Background technology
Shape memory effect is meant that alloy material passes through martensitic transformation, in low temperature (martensite) distortion, reaches a high temperature (parent phase) through heating, and alloy material returns to the original-shape before the distortion.In numerous shape memory alloy systems, the TiNi alloy is with its good memory effect, and mechanical property and wear resistant corrosion resistant obtain extensive studies and application, are the most successful current most important a kind of memorial alloys.
Utilize shape memory alloy to be heated and undergo phase transition, can remember and recover the characteristics of original-shape, people wish to make the collection perception and are the intelligent element of one with driving, it has volume little, and cost is low, and is simple in structure, alternative complex electromechanical systems such as can use at advantage under complex environment; Yet, the temperature that shape memory alloy undergoes phase transition is unsettled, this has just had a strong impact on the reliability of memorial alloy product application, the commercialization that has restricted memorial alloy is used, therefore, solve the problem of stable phase change temperature, become the bottleneck problem of restriction memorial alloy product popularization and application.
The main in the world at present method that adopts hot mechanical training, obtain the stable transformation temperature of memorial alloy, this method is stretched to certain deflection with the memory alloy wire material, under this state, heat repeatedly, cool off, promptly undergo phase transition repeatedly, the main deficiency of this method is that alloy material must be through heating, cooling off repeatedly, the training process cycle is long, the cost height will constitute damage to material during aximal deformation value, be not suitable for industrial production.
Summary of the invention
The object of the present invention is to provide a kind of cycle of training short, to the material not damaged, can make the stable mechanical training method for Ti-Ni marmem of martensitic transformation temperature.
Technical scheme of the present invention is:
With Ti-Ni alloy (wherein the Ni atomic percentage conc is 49～51at%, the Ti surplus), the mode tension and compression symmetry repeatedly that adopts strain to control is executed and is carried, and concrete steps are as follows:
1. adopt vacuum induction melting to become alloy cast ingot the Ti-Ni alloy, through diffusion annealing forge hot or hot-roll forming, again through solid solution and ageing treatment, air cooling obtains martensitic phase to room temperature, measures yield strength value;
2. adopting symmetrical tension and compression to load under the room temperature, is Δ ε with the plastix strain width of cloth
p=10
-4～5 * 10
-3Strain control, load ratio λ=-1, waveform is a choppy sea, frequency is 0.1～10Hz, executes repeatedly that to carry a number of times be the material saturated stress number of times that circulates, and is 3000～5000 times, thereby obtains the stable Ti-Ni marmem of martensitic transformation temperature.
Diffusion annealing described in the step 1, temperature is: 900 ± 20 ℃, soaking time is: 3～10h/25mm; Described solution treatment, temperature are 750 ± 10 ℃, and the time is 30min～1h; Described ageing treatment, temperature are 400 ± 10 ℃, and the time is 30min～3h; It can also be the stress control of 1 ± 5% times of yield strength with load that symmetrical tension and compression described in the step 2 load.
Advantage of the present invention is as follows:
1. the present invention is carried by executing repeatedly, obtains the shape memory alloy of stable phase change temperature, has overcome traditional hot mechanical training method and need heat the refrigerative limitation, has shortened the training time greatly, and save energy reduces the training cost.
2. the present invention can select Ti-Ni marmem bar or sheet material for use, and material does not need aximal deformation value, thereby material is not caused damage, and suitable industrial application.
Description of drawings
Fig. 1 is the relative resistance-temperature curve of material after the embodiment of the invention 1 solid solution, the ageing treatment.
Fig. 2 is the relative resistance-temperature curve of the embodiment of the invention 1 circulation back material.
Fig. 3 is the temperature-cyclic curve of the embodiment of the invention 1 circulation back material.
Fig. 4 is comparative example and embodiment 1 correlated temperature-cyclic curve.
Embodiment
Be described in further detail the present invention below by embodiment and accompanying drawing.
Embodiment 1
With the Ti-49.6Ni shape memory alloy is example, and this material becomes the Ti-49.6at%Ni alloy cast ingot through vacuum induction melting, the heavy 10kg of ingot; Behind 900 ℃ of diffusions (homogenizing) annealing 3h, be rolled into the bar that diameter is 11mm, through 750 ℃ of solution treatment 30min, 400 ℃ of ageing treatment 1h, air cooling is to room temperature, and this material room temperature is a martensitic phase, and its room temperature tensile yield strength is 187MPa, be illustrated in figure 1 as the relative resistance-temperature curve of material after solid solution, the ageing treatment, the double as seen from the figure martensitic transformation temperature that records is unsettled; Adopt the control of the plastix strain width of cloth, the tension and compression of room temperature symmetry load plastix strain width of cloth Δ ε
p=5 * 10
4, load ratio λ=-1, waveform is a choppy sea, and frequency is 0.5Hz, and this plastix strain value is corresponding to YIELD STRENGTH 187MPa.
Be the relative resistance-temperature curve of embodiment 1 circulation back material as shown in Figure 2, as seen from the figure, the double martensitic transformation temperature that records coincide goodishly;
Fig. 3 is the temperature-cyclic curve of embodiment 1 circulation back material, as seen from the figure, the present embodiment saturated stress number of times that circulates is 3000 times, the martensitic transformation temperature of the different cycle indexes in saturated back show quite stable, can obtain stable martensitic transformation temperature.
The present invention is not limited to above embodiment, and the present invention can also be the stress control of 1 ± 5% times of yield strength with load, under the condition that does not break away from spirit and scope of the invention, can make various changes and modifications to the present invention.
Comparative example
Difference from Example 1 is:
Executing with stress control and to carry, is σ=100MPa (this moment, stress amplitude was only a little more than half of yield strength value) circulation by stress amplitude, and other conditions are constant, as seen from Figure 4, compare with embodiment 1 curve, and its martensitic transformation temperature is fluctuation status.
Claims (5)
1. mechanical training method for Ti-Ni marmem, the Ni atomic percentage conc is 49～51at% in the Ti-Ni alloy, the Ti surplus is characterized in that: execute with strain control mode tension and compression symmetry repeatedly and carry, concrete steps are as follows:
1) adopt vacuum induction melting to become alloy cast ingot the Ti-Ni alloy, through diffusion annealing, forge hot or hot-roll forming, again through solid solution and ageing treatment, air cooling obtains martensitic phase to room temperature, measures its yield strength value;
2) adopting symmetrical tension and compression to load under the room temperature, is Δ ε with the plastix strain width of cloth
p=10
-4～5 * 10
-3Strain control, load ratio λ=-1, waveform is a choppy sea, frequency is 0.1～10Hz, executes repeatedly that to carry a number of times be the material saturated stress number of times that circulates, and is 3000～5000 times, thereby obtains the stable Ti-Ni marmem of martensitic transformation temperature.
2. according to the described mechanical training method for Ti-Ni marmem of claim 1, it is characterized in that: step 2) described in symmetrical tension and compression to load with load be the stress control of 1 ± 5% times of yield strength.
3. according to claim 1 or 2 described mechanical training method for Ti-Ni marmem, it is characterized in that: diffusion annealing described in the step 1), temperature is: 900 ± 20 ℃, soaking time is: 3～10h/25mm.
4. according to claim 1 or 2 described mechanical training method for Ti-Ni marmem, it is characterized in that: solution treatment described in the step 1), temperature are 750 ± 10 ℃, and the time is 30min～1h.
5. according to claim 1 or 2 described mechanical training method for Ti-Ni marmem, it is characterized in that: ageing treatment described in the step 1), temperature are 400 ± 10 ℃, and the time is 30min～3h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB011281294A CN1139667C (en) | 2001-09-05 | 2001-09-05 | Mechanical training method for Ti-Ni marmem |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB011281294A CN1139667C (en) | 2001-09-05 | 2001-09-05 | Mechanical training method for Ti-Ni marmem |
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| Publication Number | Publication Date |
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| CN1403611A true CN1403611A (en) | 2003-03-19 |
| CN1139667C CN1139667C (en) | 2004-02-25 |
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|---|---|---|---|
| CNB011281294A Expired - Fee Related CN1139667C (en) | 2001-09-05 | 2001-09-05 | Mechanical training method for Ti-Ni marmem |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103014414A (en) * | 2013-01-04 | 2013-04-03 | 哈尔滨工程大学 | TiNi-base shape memory alloy containing components in graded distribution and preparation method thereof |
| CN104388754A (en) * | 2014-12-15 | 2015-03-04 | 苏州宽温电子科技有限公司 | Shape memory alloy |
| CN104480348A (en) * | 2014-12-06 | 2015-04-01 | 李钰瑾 | NiTi shape memory alloy material as well as preparation method and application thereof and automatic fire-fighting alarming detector |
| US9476113B1 (en) | 2010-09-02 | 2016-10-25 | The United States Of America As Represented By The Administrator Of National Aeronautics And Space Administration | Thermomechanical methodology for stabilizing shape memory alloy (SMA) response |
| CN109112356A (en) * | 2018-08-03 | 2019-01-01 | 燕山大学 | A kind of high-strength corrosion-resistant erosion titanium alloy and preparation method thereof |
| CN109913764A (en) * | 2019-04-10 | 2019-06-21 | 四川大学 | A method of improving ferrimanganic alumel memory performance stability |
| CN112058934A (en) * | 2020-09-11 | 2020-12-11 | 上海交通大学 | Preparation process of die-penetrating tip in shape memory alloy wire drawing process |
| CN116516270A (en) * | 2023-04-03 | 2023-08-01 | 华南理工大学 | Two-step training method for efficiently improving nickel-titanium alloy double-pass shape memory effect |
-
2001
- 2001-09-05 CN CNB011281294A patent/CN1139667C/en not_active Expired - Fee Related
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9476113B1 (en) | 2010-09-02 | 2016-10-25 | The United States Of America As Represented By The Administrator Of National Aeronautics And Space Administration | Thermomechanical methodology for stabilizing shape memory alloy (SMA) response |
| CN103014414A (en) * | 2013-01-04 | 2013-04-03 | 哈尔滨工程大学 | TiNi-base shape memory alloy containing components in graded distribution and preparation method thereof |
| CN103014414B (en) * | 2013-01-04 | 2014-08-20 | 哈尔滨工程大学 | TiNi-base shape memory alloy containing components in graded distribution and preparation method thereof |
| CN104480348A (en) * | 2014-12-06 | 2015-04-01 | 李钰瑾 | NiTi shape memory alloy material as well as preparation method and application thereof and automatic fire-fighting alarming detector |
| CN104388754A (en) * | 2014-12-15 | 2015-03-04 | 苏州宽温电子科技有限公司 | Shape memory alloy |
| CN109112356A (en) * | 2018-08-03 | 2019-01-01 | 燕山大学 | A kind of high-strength corrosion-resistant erosion titanium alloy and preparation method thereof |
| CN109913764A (en) * | 2019-04-10 | 2019-06-21 | 四川大学 | A method of improving ferrimanganic alumel memory performance stability |
| CN112058934A (en) * | 2020-09-11 | 2020-12-11 | 上海交通大学 | Preparation process of die-penetrating tip in shape memory alloy wire drawing process |
| CN112058934B (en) * | 2020-09-11 | 2022-01-18 | 上海交通大学 | Preparation process of die-penetrating tip in shape memory alloy wire drawing process |
| CN116516270A (en) * | 2023-04-03 | 2023-08-01 | 华南理工大学 | Two-step training method for efficiently improving nickel-titanium alloy double-pass shape memory effect |
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| Publication number | Publication date |
|---|---|
| CN1139667C (en) | 2004-02-25 |
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