CN1763233A - Wide heat stagnation TiNi base marmem dead ring and preparation method and application - Google Patents
Wide heat stagnation TiNi base marmem dead ring and preparation method and application Download PDFInfo
- Publication number
- CN1763233A CN1763233A CN 200410050655 CN200410050655A CN1763233A CN 1763233 A CN1763233 A CN 1763233A CN 200410050655 CN200410050655 CN 200410050655 CN 200410050655 A CN200410050655 A CN 200410050655A CN 1763233 A CN1763233 A CN 1763233A
- Authority
- CN
- China
- Prior art keywords
- dead ring
- wide heat
- heat stagnation
- base marmem
- ring
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910010380 TiNi Inorganic materials 0.000 title claims abstract description 22
- 238000002360 preparation method Methods 0.000 title claims abstract description 8
- 238000002844 melting Methods 0.000 claims abstract description 10
- 230000008018 melting Effects 0.000 claims abstract description 10
- 238000005266 casting Methods 0.000 claims abstract description 7
- 230000006698 induction Effects 0.000 claims abstract description 7
- 238000000137 annealing Methods 0.000 claims abstract description 3
- 238000005242 forging Methods 0.000 claims abstract description 3
- 238000005098 hot rolling Methods 0.000 claims abstract description 3
- 230000003446 memory effect Effects 0.000 claims description 5
- 230000008602 contraction Effects 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 27
- 239000000956 alloy Substances 0.000 abstract description 27
- 238000011084 recovery Methods 0.000 abstract description 7
- 238000009434 installation Methods 0.000 abstract description 3
- 238000000034 method Methods 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 3
- 238000005476 soldering Methods 0.000 abstract description 3
- 238000005275 alloying Methods 0.000 description 13
- 239000000470 constituent Substances 0.000 description 10
- 230000009466 transformation Effects 0.000 description 8
- 239000011159 matrix material Substances 0.000 description 5
- 229910001285 shape-memory alloy Inorganic materials 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- 239000007787 solid Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- 230000006386 memory function Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000001816 cooling Methods 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
- 230000000694 effects Effects 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000007334 memory performance Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000032258 transport Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Images
Landscapes
- Forging (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The present invention discloses a kind of wide heat stagnation TiNi base marmem dead ring and preparation method and application.By atomic percent, alloy compositions is Ti:42-47; Ni:44-49; Nb:6-13; Zr:0.1-3.Its preparation method: 1) melting: by described component, adopt the melting of vacuum medium-frequency induction furnace, the cast ingot casting; 2) homogenizing is handled: 800 ℃～1000 ℃ of temperature, 3～5 hours time; 3) 800 ℃～900 ℃ forgings; 4) 800 ℃～900 ℃ hot rollings; 5) annealing: 800 ℃～900 ℃ of temperature, 10～60 minutes time, stove is chilled to room temperature; 6) be processed into finished product.The present invention utilizes the recovery characteristics of memorial alloy, realizes being fastenedly connected, and dead ring strength of joint height, it is little to connect resistance.Compare with common soldering, rubber circle and other machine riveting methods, have advantages such as volume is little, in light weight, easy for installation and safe and reliable.
Description
Technical field
The present invention relates to wide heat stagnation TiNi base marmem and be fastenedly connected technology, belong to the shape memory alloy field of material specialty, especially a kind of wide heat stagnation TiNi base marmem dead ring and preparation method and application.
Background technology
At present, the connection that is used for line, pipe, cable mainly is a mechanical connection, General fasteners fastening.Its shortcoming is operation inconvenience, unbalance stress, and stopping property is poor, yielding inefficacy.Particularly in mechanics of communication and telltale, run into the sealing of metal thin-wall and metal, pottery and plastic end enclosure through regular meeting.On technology, be difficult to realize by traditional soldering and machine riveting.
In the TiNi of prior art base marmem, be used for the memorial alloy that pipe connection uses and have only Ti50Ni47Fe3 (atomic percent) and two kinds of alloys of Ti44Ni47Nb9 (atomic percent), the salient features of these two kinds of alloys sees Table 1.
Table 1
| Alloying constituent (at.%) | Room-temperature mechanical property | Transformation temperature | ||
| σ 0.2(MPa) | δ(％) | Ms(℃) | As(℃) | |
| Ti50Ni47Fe3 | 450 | 12 | -160 | -130 |
| Ti44Ni47Nb9 | 500 | 56 | -90 | -51 |
The Ti50Ni47Fe3 alloy is a kind of single-phased alloy, and (δ .%) is lower for its unit elongation, can not bear big hole enlargement deflection.After low temperature hole enlargement distortion, the starting temperature A ' s point that its martensite reverse changes to parent phase is below-50 ℃, so can only use very inconvenient in hole enlargement under the liquid nitrogen temperature, storage, transportation and installation by the tube stub of its making.Ti44Ni47Nb9 is a kind of two phase alloys, U.S. Patent number 4770725 (1988), by matrix phase (parent phase) and rich niobium mutually (β-Nb phase) form, behind low-temperature deformation, about 40 ℃, be higher than common room temperature at its A ' s o'clock, but still undesirable in hot environment.In addition, owing to be subjected to the restriction of alloy strength, for requiring high strength of joint, especially closely arrange the space at pipeline, when requiring thin-walled tube joint web member, the TiNiNb alloy can not satisfy the demands.Still find no the wide heat stagnation shape memory alloy of interpolation the 4th or The Fifth Element through the Searches of Patent Literature.
Summary of the invention
The objective of the invention is to overcome the deficiencies in the prior art, a kind of wide heat stagnation TiNi base marmem dead ring and preparation method and application with higher fastening strength and sealing property is provided.
Technical scheme of the present invention is:
A kind of wide heat stagnation TiNi base marmem dead ring, by atomic percent, its component is:
Ti：42-47；Ni：44-49；Nb：6-13；Zr：0.1-3。
Described wide heat stagnation TiNi base marmem dead ring, its component can also comprise Mo:0.1-3.Described Zr:0.1-3 can replace by Mo:0.1-3; Described Zr:0.1-3 can replace by V:0.1-3; Described Zr:0.1-3 can replace by Cr:0.1-3; Described Zr:0.1-3 can replace by Al:0.1-3.
Described wide heat stagnation TiNi base marmem dead ring, ring be shaped as circle, ellipse, Polygons, rectangle or trilateral; The cross-sectional shape of ring is circle, ellipse, Polygons, rectangle or trilateral; The sectional area 2mm of ring
2-1600mm
2In the scope, the girth of ring is in the 6-1470mm scope.
The preparation method of described wide heat stagnation TiNi base marmem dead ring, step is as follows:
1) melting: by described component, adopt the melting of vacuum medium-frequency induction furnace, the cast ingot casting;
2) homogenizing is handled: 800 ℃～1000 ℃ of temperature, 3～5 hours time;
3) 800 ℃～900 ℃ forgings;
4) 800 ℃～900 ℃ hot rollings or 800 ℃～900 ℃ extruding;
5) annealing: 800 ℃～900 ℃ of temperature, 10～60 minutes time;
6) be processed into finished product.
Principle of the present invention is as follows:
The principle of work of wide heat stagnation TiNi base marmem dead ring is based on the shape memory effect of memory alloy element, dead ring mechanical workout or be welded under the parent phase state, the internal diameter of its dead ring is littler than the external diameter of connected piece, makes 0.1～0.2 millimeter of the external diameter of the internal diameter 〉=web member of dead ring with the mechanical means hole enlargement.Dead ring during assembling after room temperature is with hole enlargement is enclosed within connecting portion, postheating, because shape memory effect, dead ring is subjected to thermal contraction, returns to the preceding state of hole enlargement.Because the internal diameter of dead ring is littler than the external diameter of connected piece before the hole enlargement, produce big shrink range cooperation and make joint fastening, realize connecting.
In addition, the matrix in the TiNiNb alloy is mainly elementary composition by Ti and Ni mutually, and contains small amount of N b, so the selection of alloying element should be taken into account that they have certain solid solubility at matrix in mutually, performance solution strengthening effect.The add-on of alloying element should be controlled in their the solid solubility scope, avoids forming precipitated phase, otherwise will have a strong impact on its shape memory function and processing characteristics.For this reason, we have selected Zr, V, Al, Mo and Cr, and as the X element in the TiNiNb-X alloy, wherein Zr has identical crystalline structure with Ti, and V and Al have very high solid solubility in Ti, and Mo and Cr have very high solid solubility in Ni.Select these alloying elements partly to replace Ti or Ni in the TiNiNb alloy respectively, higher intensity and the memory performance and the higher A ' s point of memorial alloy performance of the new component that is constituted.
Advantage of the present invention and beneficial effect are as follows:
1, the present invention utilizes the recovery characteristics of memorial alloy, realize being fastenedly connected, and the strength of joint height, it is little to connect resistance, compares with common soldering, rubber circle and other machine riveting methods, has advantages such as volume is little, in light weight, easy for installation and safe and reliable.
2, adopt the present invention stressed evenly, tightness is good, and is easy and simple to handle.
3, the present invention can at room temperature store, transports and install, and is more suitable for execute-in-place.
4, the present invention has good corrosion resisting property and stability.
Description of drawings
Fig. 1 is the metallographic structure of general T i44Ni47Nb9 ternary shape memory alloy.
Fig. 2 is the metallographic structure of Ti44Ni47Nb8.5Zr0.5 alloy among the embodiment 1.
Fig. 3 is the metallographic structure of Ti44Ni47Nb8.5Mo0.5 alloy among the embodiment 2.
Embodiment
The wide heat stagnation TiNi base marmem of the present invention dead ring:
1, ring is shaped as circle, ellipse, Polygons, rectangle or trilateral.
2, Huan cross-sectional shape is circle, ellipse, Polygons, rectangle or trilateral.
3, Huan sectional area 2mm
2-1600mm
2In the scope.
4, Huan girth is in the 6-1470mm scope.
Require: the fit-up gap is about 0.1mm, and the free amount of recovery of dead ring internal diameter is about 1.0mm, establishes the strain parameter value ε p=13% of memory effect, dead ring thickness t=1.5mm, shrink range δ=4%.Shrink range definition: δ=(φ
Quilt-D
11)/φ
Quilt* 100%
φ
QuiltBe the connected piece diameter; D
11For dead ring freely recovers the back internal diameter; D
1For protecting back, footpath dead ring internal diameter.
If the cable splice external diameter is φ 20mm, then the size of dead ring is calculated as follows:
By δ=(20-D
11)/20=4%;
The internal diameter that gets after dead ring freely recovers is D
11=19.2mm;
Select then that the internal diameter of dead ring is after the hole enlargement: D for use
1=20.1mm;
εp＝(D
1-D
0)/(D
0+t)＝13％；
So the employing internal diameter is D
0=17.62mm memory is closed dead ring and can be met the demands.
Embodiment 1
Adopt vacuum induction melting, ingot casting is handled 3h through 800 ℃～1000 ℃ evenly heatings, 800 ℃～900 ℃ of forge hots become the bar of φ 40mm, be bundled into the bar of φ 20mm through 800 ℃～900 ℃ of heat again, through 850 ℃, air cooling is to room temperature after 30 minutes, car is made sample, measure mechanical properties-55 ℃, room temperature and 300 ℃ respectively, the results are shown in table 2, σ in the table
0.2Be yield strength, δ is a unit elongation.The part sample is measured recovery of shape strain stress r and A ' s temperature after-65 ℃ of following predeformation, the result also lists in table 2, and ε t is total predeformation amount in the table, and ε r is the recovery of shape strain.
Table 2. embodiment 1 alloy mechanical property
| Embodiment | Alloying constituent .at% | -55℃ | Room temperature | 300℃ | Transformation temperature | Memory function | ||||||
| σ 0.2 MPa | δ ％ | σ 0.2 MPa | δ ％ | σ 0.2 MPa | δ ％ | Ms ℃ | As ℃ | εt ％ | εr ％ | A′s ℃ | ||
| 1 | Ti44Ni47N b8.5Zr0.5 | 292 | 35 | 550 | 50 | 445 | 60 | -88 | -52 | 16 | 7.5 | 71 |
Embodiment 2
Adopt vacuum induction melting, ingot casting is handled 3h through 900 ℃ of evenly heatings, 840 ℃ of forge hots become the bar of φ 40mm, be bundled into the bar of φ 20mm again through 860 ℃ of heat, through 850 ℃, stove is chilled to room temperature after 30 minutes, car is made sample, measure mechanical properties-55 ℃, room temperature and 300 ℃ respectively, the results are shown in table 2 simultaneously, σ in the table
0.2Be yield strength, δ is a unit elongation.The part sample is measured recovery of shape strain stress r and A ' s temperature after-65 ℃ of following predeformation, the result also lists in table 2, and ε t is total predeformation amount in the table, and ε r is the recovery of shape strain.
Table 3. embodiment 2 alloy mechanical properties
| Embodiment | Alloying constituent .at% | -55℃ | Room temperature | 300℃ | Transformation temperature | Memory function | ||||||
| σ 0.2 MPa | δ ％ | σ 0.2 MPa | δ ％ | σ 0.2 MPa | δ ％ | Ms ℃ | As ℃ | εt ％ | εr ％ | A′s ℃ | ||
| 2 | Ti44Ni47N b8.5Mo0.5 | 292 | 35 | 550 | 50 | 445 | 60 | -88 | -52 | 16 | 7.5 | 71 |
Fig. 1 is the metallographic structure of general T i44Ni47Nb9 ternary shape memory alloy, and white portion is the matrix phase, and black region is the eutectic area by matrix phase and rich niobium phase composite.Fig. 2 is the metallographic structure of Ti44Ni47Nb8.5Zr0.5 alloy among the embodiment 1, and Fig. 3 is the metallographic structure of Ti44Ni47Nb8.5Mo0.5 alloy among the embodiment 2.Under identical magnification, the microstructure of back two kinds of alloys is obviously thin many than the former.
Embodiment 3～5
Adopt embodiment 2 described methods to prepare alloy, measure the mechanical property of its room temperature, the results are shown in shown in the table 4.
Table 4. embodiment 3～5 alloy mechanical properties
| Embodiment | Alloying constituent .at% | Room temperature | |
| σ 0.2，MPa | δ，％ | ||
| 3 | Ti44Ni47Nb8.5Cr0.5 | 606 | 50 |
| 4 | Ti44Ni47Nb8.5V0.5 | 535 | 73 |
| 5 | Ti44Ni47Nb8.5Al0.5 | 586 | 75 |
Embodiment 6
Adopt vacuum induction melting, ingot casting is handled 5h through 1000 ℃ of evenly heatings, and 800 ℃ of forge hots become the bar of φ 40mm, be squeezed into the bar of φ 30mm again through 880 ℃ of jackets, through 800 ℃, stove is chilled to room temperature after 40 minutes, car is made sample, and embodiment 6～10 alloying constituents and transformation temperature see Table 5.
Table 5. embodiment 6 alloying constituents and transformation temperature
| Embodiment | Alloying constituent, at% | Ms，℃ | As，℃ | Processing characteristics |
| 6 | Ti44Ni47Nb8.5Zr0.5 | -63 | -37 | Good |
Embodiment 7～14
Adopt vacuum induction melting, ingot casting is handled 4h through 950 ℃ of evenly heatings, and 840 ℃ of forge hots become the bar of φ 40mm, through 850 ℃ of bars that are rolled into φ 20mm, through 900 ℃, stove is chilled to room temperature after 20 minutes again, car is made sample, and embodiment 7～14 alloying constituents and transformation temperature see Table 6.
Table 6. embodiment 7～14 alloying constituents and transformation temperature
| Embodiment | Alloying constituent, at% | Ms，℃ | As，℃ | Processing characteristics |
| 7 | Ti44Ni47Nb8.5Cr0.5 | ＜150 | - | Better |
| 8 | Ti44Ni47Nb8.5V0.5 | -74 | -42 | Better |
| 9 | Ti44Ni47Nb8.5Al0.5 | ＜150 | - | Better |
| 10 | Ti46Ni47Nb6V1 | 7 | 30 | Better |
| 11 | Ti46Ni47Nb6Zr1 | 15 | 31 | Good |
| 12 | Ti46Ni47Nb6Cr1 | ＜-150 | - | Better |
| 13 | Ti46Ni47Nb6Mo1 | -19.5 | -10 | Better |
| 14 | Ti46Ni47Nb6Al1 | -24 | -13.5 | Difference |
Press table 5,6 listed composition alloyages, the transformation temperature of measuring each alloy sees Table 5,6.Result in the table has shown: selected different Ti/Ni content ratios or selected different alloy elements, Ms point temperature is changed in-150 ℃ to 30 ℃ scopes.
Adopt above-mentioned memorial alloy to prepare dead ring, make 0.1～0.2 millimeter of the external diameter of the internal diameter 〉=web member of dead ring with the mechanical means hole enlargement, during assembling, the dead ring after room temperature is with hole enlargement is enclosed within connecting portion, postheating, because shape memory effect, dead ring is subjected to thermal contraction, returns to the preceding state of hole enlargement, because the internal diameter of dead ring is littler than the external diameter of connected piece before the hole enlargement, produce big shrink range cooperation and make joint fastening, realize connecting.
Claims (9)
1. one kind wide heat stagnation TiNi base marmem dead ring is characterized in that by atomic percent its component is:
Ti：42-47；Ni：44-49；Nb：6-13；Zr：0.1-3。
2. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that comprising Mo:0.1-3.
3. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that described Zr:0.1-3 replaces with Mo:0.1-3.
4. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that described Zr:0.1-3 replaces with V:0.1-3.
5. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that described Zr:0.1-3 replaces with Cr:0.1-3.
6. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that described Zr:0.1-3 replaces with Al:0.1-3.
7. according to the described wide heat stagnation TiNi base marmem dead ring of claim 1, it is characterized in that: ring be shaped as circle, ellipse, Polygons, rectangle or trilateral; The cross-sectional shape of ring is circle, ellipse, Polygons, rectangle or trilateral; The sectional area 2mm of ring
2-1600mm
2In the scope, the girth of ring is in the 6-1470mm scope.
8,, it is characterized in that step is as follows according to the preparation method of the described wide heat stagnation TiNi base marmem dead ring of claim 1:
1) melting: by described component, adopt the melting of vacuum medium-frequency induction furnace, the cast ingot casting;
2) homogenizing is handled: 800 ℃～1000 ℃ of temperature, 3～5 hours time;
3) 800 ℃～900 ℃ forgings;
4) 800 ℃～900 ℃ hot rollings or 800 ℃～900 ℃ extruding;
5) annealing: 800 ℃～900 ℃ of temperature, 10～60 minutes time;
6) be processed into finished product.
9, according to the application of claim 1 or 7 described wide heat stagnation TiNi base marmem dead rings, it is characterized in that dead ring is made with the mechanical means hole enlargement at low temperature 0.1～0.2 millimeter of the external diameter of the internal diameter 〉=web member of dead ring, during assembling, dead ring after room temperature is with hole enlargement is enclosed within connecting portion, postheating, because shape memory effect, dead ring is subjected to thermal contraction, return to the preceding state of hole enlargement, because the internal diameter of dead ring is littler than the external diameter of connected piece before the hole enlargement, produce big shrink range cooperation and make joint fastening, realize connecting.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100506556A CN100348760C (en) | 2004-10-22 | 2004-10-22 | Fastening ring made of wide thermal hysteresis Ti-Ni-based shape-memory alloy, preparation method and application thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100506556A CN100348760C (en) | 2004-10-22 | 2004-10-22 | Fastening ring made of wide thermal hysteresis Ti-Ni-based shape-memory alloy, preparation method and application thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1763233A true CN1763233A (en) | 2006-04-26 |
| CN100348760C CN100348760C (en) | 2007-11-14 |
Family
ID=36747551
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004100506556A Expired - Fee Related CN100348760C (en) | 2004-10-22 | 2004-10-22 | Fastening ring made of wide thermal hysteresis Ti-Ni-based shape-memory alloy, preparation method and application thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100348760C (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102296224A (en) * | 2010-06-24 | 2011-12-28 | 沈阳天贺新材料开发有限公司 | Wide thermal hysteresis TiNiNb shape memory alloy memory ring and preparation method and application thereof |
| 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 |
| CN104060145A (en) * | 2014-07-10 | 2014-09-24 | 哈尔滨工程大学 | TiNiNbB shape memory alloy and preparation method thereof |
| CN106601505A (en) * | 2016-11-08 | 2017-04-26 | 国家电网公司 | Shape memory alloy plum blossom contact |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000079432A (en) * | 1998-09-03 | 2000-03-21 | Furukawa Techno Material:Kk | Nickel-titanium-based shape memory alloy made joined ring and its manufacture |
| KR100395588B1 (en) * | 2000-07-07 | 2003-08-25 | 주식회사 바이오스마트 | Shape memory alloy in Ti-Ni-Cu-Mo |
| CN1164782C (en) * | 2001-12-25 | 2004-09-01 | 中国科学院金属研究所 | Vacuum induction smelting process of Ti-Ni and Ti-Ni-Nb marmem |
| CN1209477C (en) * | 2003-10-16 | 2005-07-06 | 上海交通大学 | Micro fine-grained titanium-nickel-niobium shape memory alloy block material preparing method |
-
2004
- 2004-10-22 CN CNB2004100506556A patent/CN100348760C/en not_active Expired - Fee Related
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102296224A (en) * | 2010-06-24 | 2011-12-28 | 沈阳天贺新材料开发有限公司 | Wide thermal hysteresis TiNiNb shape memory alloy memory ring and preparation method and application thereof |
| 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 |
| CN104060145A (en) * | 2014-07-10 | 2014-09-24 | 哈尔滨工程大学 | TiNiNbB shape memory alloy and preparation method thereof |
| CN106601505A (en) * | 2016-11-08 | 2017-04-26 | 国家电网公司 | Shape memory alloy plum blossom contact |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100348760C (en) | 2007-11-14 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105734322B (en) | A kind of preparation method of carbon nanotube enhanced aluminium-based composite material | |
| CN1772932A (en) | High temperature Titanium alloy with high creepage resistance and high fatigue strength | |
| CN101910443B (en) | Method for producing copper-free aluminum alloy forging products | |
| CN106967900B (en) | A kind of titanium-based metal glass particle reinforced aluminum matrix composites and preparation method thereof | |
| CN105331858A (en) | Preparation method for high-strength and high-toughness ultra-fine grain aluminium alloy | |
| CN1833043A (en) | Austenitic stainless steel for hydrogen gas and method for production thereof | |
| CN101078079A (en) | High-intensity thermal deformation resistant magnesium alloy | |
| CN1743483A (en) | Ni-Cr-Co alloy for advanced gas turbine engines | |
| CN1258756A (en) | High-temperature high-strength antioxidant anticorrosive austenite alloy | |
| CN109317667B (en) | Preparation method of hybrid aluminum-based composite pipe | |
| CN101654753B (en) | TiNiNb/NbTi memory alloy composite material and preparation method thereof | |
| CN108251724A (en) | Suitable for the high strength heat resistant alloy and preparation process of big specification Complicated structure casting | |
| CN102304653A (en) | High-plasticity two-phase yttrium-containing magnesium-lithium-aluminum alloy and preparation method thereof | |
| CN112962005A (en) | Preparation method of high-strength high-thermal-conductivity aluminum alloy | |
| CN1599803A (en) | Ferritic stainless steel for use in high temperature applications and method for producing a foil of the steel | |
| CN1683097A (en) | Heat keeping and forging and blank cogging method for GH742 alloy large steel ingot | |
| CN102251146B (en) | Nickel-titanium-aluminum-based high-temperature alloy material and isothermal forging preparation method thereof | |
| CN110508735B (en) | Increment constraint multidirectional forging method for silicon carbide whisker reinforced aluminum matrix composite | |
| CN103341700B (en) | A kind of Co-Ti-Nb system high-temp solder | |
| CN102000944B (en) | Method for forming Ti3Al-based alloy thin-wall barrel | |
| CN106057356A (en) | Preparation method of CuNb reinforced Nb3Sn low-temperature superconducting wire fabricated by bronze process | |
| US6756133B2 (en) | High temperature aluminum alloy brazing sheet and methods of manufacturing and uses therefor | |
| CN1763233A (en) | Wide heat stagnation TiNi base marmem dead ring and preparation method and application | |
| CN101913022B (en) | Method for welding dissimilar materials of TA15 titanium alloy and chromium bronze through electron beams | |
| CN103014412A (en) | Composite heat-resistant titanium alloy |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20071114 Termination date: 20161022 |