EP0062365A1 - Procédé de fabrication d'un élément de construction en un alliage à base de titane, ainsi que l'élément et son application - Google Patents

Procédé de fabrication d'un élément de construction en un alliage à base de titane, ainsi que l'élément et son application Download PDF

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Publication number
EP0062365A1
EP0062365A1 EP82200313A EP82200313A EP0062365A1 EP 0062365 A1 EP0062365 A1 EP 0062365A1 EP 82200313 A EP82200313 A EP 82200313A EP 82200313 A EP82200313 A EP 82200313A EP 0062365 A1 EP0062365 A1 EP 0062365A1
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EP
European Patent Office
Prior art keywords
temperature
phase
titanium
deformation
alloy
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Granted
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EP82200313A
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German (de)
English (en)
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EP0062365B1 (fr
Inventor
Joachim Dr. Albrecht
Thomas Dr. Duerig
Dag Richter
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BBC Brown Boveri AG Switzerland
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BBC Brown Boveri AG Switzerland
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Publication of EP0062365A1 publication Critical patent/EP0062365A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/006—Resulting in heat recoverable alloys with a memory effect

Definitions

  • the invention relates to a method for producing a component from a titanium alloy according to the preamble of claim 1, and a component according to the preamble of claim 11 and the use of a component according to the preamble of claim 18.
  • Ni / Ti e.g. Buehler, WJ Cross, WB: 55 Nitinol, unique wire alloy with a memory. Wire J. 2 (1969), p. 41 - 49
  • Ni / Ti / Cu the copper-rich or nickel-rich alloys of the ⁇ -brass type based on Cu / Zn / Al, Cu / Al, Cu / Al / Ni with Ni / Al
  • a shape memory effect has also been discovered and described in a superconducting titanium alloy containing 35% niobium (see Baker, C .: The shape memory effect in a titanium 35 wt% niobium alloy. Metal Sci. J. 5 (1971), p. 92 -100).
  • Memory alloys based on Ni / Ti have a temperature M S of martensitic conversion of theoretically at most 80 ° C (practically usually not above 50 ° C), which is too low for many applications, especially in the field of electrical thermal switches.
  • such alloys are expensive, especially if one also takes into account the expensive manufacture of components.
  • the copper alloys belonging to the ⁇ -brass type such as Cu / Al / Ni have a tensile strength which is too low for many practical applications with a maximum of 600 MPa.
  • their M S temperature is heavily dependent on the accuracy of the composition - in particular on the aluminum content - which makes their reproducibility difficult. Because it is the aluminum that, due to its high vapor pressure, causes losses that are difficult to control and thus deviations from the melting of the alloys Setpoint analysis leads.
  • the invention has for its object to provide a manufacturing method for a component made of a titanium alloy and a component and its use, which makes use of the martensitic conversion for the purpose of achieving a memory effect. There is also the task of characterizing the memory effect in its various manifestations in more detail and demonstrating its usability in technology.
  • FIG. 1 shows a section of a schematic, subsumed phase diagram of a binary titanium alloy. It is the titanium page. The ordinate represents the temperature scale and at the same time corresponds to 100% Ti, ie 0% alloying element. The alloy element X is plotted on the abscissa in percent (for example% by weight). The solid curves divide the diagram into the ⁇ -, ( ⁇ + ⁇ ) - and ⁇ -phase area. Two further curves M S and M d , drawn in dashed lines, are related to the phase transition (martensite formation) occurring during quenching from the ⁇ region and are explained in more detail below. You meet the 0 ° C isotherm (abscissa) in points A and B.
  • FIG. 2 shows a diagram in which the course of the recoverable strain r (%) as a function of the primary permanent strain ⁇ (%) is shown as curve a for a titanium alloy.
  • line b for ideal recovery (100%) is drawn as a 45 ° straight line.
  • a S is the temperature at the start of the transformation of the martensite (low temperature phase) into the high temperature phase.
  • a F represents the corresponding temperature for the end of this phase transition.
  • the arrows indicate the direction of the deformation / temperature loop.
  • the dashed line denotes the pure thermal shrinkage of the workpiece after cooling to room temperature.
  • the diagram has a fundamental character and applies qualitatively to all mechanically unstable ⁇ -titanium alloys.
  • Fig. 6 and Fig. 7 each show a test rod for tensile and. Torsion samples in the length and diameter dimensions, which need no further explanation. Accordingly, the torsion tests were carried out on hollow cylindrical test bars.
  • an electrical switch is shown schematically in section, which uses coil springs as components.
  • 1 is a housing in which a support 2 is fastened, which supports the bearing 3 for the contact lever 4.
  • 5 each represent a fixed and 6 each a movable contact.
  • the contact lever 4 is held by the springs 7 and 8 in a previously selectable rest position. This can be the location shown (both contact points open) or another location (one contact point closed).
  • 7 is a coil spring made of a memory alloy. It can be designed both as a compression spring and as a tension spring with or without tension.
  • 8 is a common coil spring, which can again act as a tension or compression spring with or without preload. Depending on the intended version of 7 and 8 and the combination of these springs used, 8 counteracts the memory effect of 7 (return or counter spring) or supports it (auxiliary spring).
  • 9 shows a schematic perspective illustration of an electrical switch using a torsion bar.
  • 9 is a base plate on which a torsion bar 10 made of memory alloy is attached at right angles.
  • the latter in turn carries the switching arm 11 at its end, the mobility (pivoting range) of which is indicated by a double arrow.
  • It has a movable contact 6 at its end, which faces a fixed contact 5 which is fastened in the holder 12.
  • 10 to 13 show the process sequence in the production of a fixed and a releasable connection.
  • 14 each represents a pipe to be connected in longitudinal section.
  • 13 is a sleeve made of a memory alloy, the inside diameter of which, in the initial state, is undersized compared to the outside pipe diameter.
  • 15 shows the sleeve during the expansion process by means of a ball 16.
  • FIG. 17 shows the sleeve after the shrinking process (one-way memory effect) above the pipes 14. This corresponds to the state of a firm pipe connection.
  • Fig. 13 shows the state after loosening (if necessary) the same connection.
  • 18 is the the sleeve is loosened again after the expansion process due to the isothermal memory effect.
  • 19 represents a disk made of a memory alloy provided with a groove 20.
  • 21 is a hollow body made of ceramic material which engages in the groove 19 in a vacuum-tight manner.
  • the disc 22 provided with a conical backward rotation 23 is made of a memory alloy.
  • the hollow body 24 to be connected, made of metal, plastic or ceramic material, is indicated by dashed lines before assembly.
  • 25 represents a disk made of a memory alloy, which is offset on both sides and each has a cylindrical undercut 23. The ends of the hollow bodies 24 can, as indicated, have different shapes. In the present case, the disc 25 serves both as a connecting element and as a partition.
  • 26 is a stepped hollow body made of memory alloy, which has the back turns 23 and a central opening 27.
  • the hollow bodies 24 to be connected can be of different diameters and of course of different materials.
  • the titanium alloys there are those that show memory effects after a suitable thermal and thermomechanical pretreatment.
  • the range of composition of these alloys is relatively narrow.
  • the first condition is that they contain at least partially the body-centered / 3-phase in the stable initial state at room temperature. Pure ⁇ alloys thus fail.
  • a further limitation in the composition is that the alloys must belong to the class of mechanically unstable / 3-titanium alloys (in the sense of this invention), which are basically defined as follows:
  • Alloy characterized by the property that its body-centered cubic ⁇ phase can be at least partially converted into the stress-induced martensitic ⁇ "phase by applying a permanent deformation.
  • this can be determined by first subjecting the beta titanium alloy to a thin sheet with a maximum thickness of 1 mm, which is then subjected to solution annealing above the ⁇ transition temperature and then within a cooling time of at most 10 seconds to go through the difference between solution annealing temperature and 100 ° C in ice water is deterred. After quenching, the material must have a maximum of 10% by volume of thermally induced martensite.
  • the alloy is characterized in that the ⁇ -phase is converted into martensite ( ⁇ ") during subsequent mechanical deformation.
  • the maximum temperature at which mechanically induced martensite ( ⁇ ") can be determined after this deformation is defined as A M d .
  • M S represents the temperature at which martensite begins to form.
  • M d has already been defined in more detail above. For the alloys in question at room temperature, there is therefore the condition that their composition must fall approximately in the range between A and B (intersection of the M S and M d line with the O O C isotherms).
  • At least one should quench from a temperature corresponding to the isothermal CD, since the above condition can no longer be met when quenching lower temperatures. This is indicated by the dash-dotted vertical on the left with an arrow. In the latter case, however, one then loses a small proportion of material indicated by the lever law, which converts into the stable ⁇ phase on the transition via the ⁇ conversion line and is lost for the memory effect. However, the conditions for the subsequent formation of martensite are still optimal for the remaining portion of the ⁇ phase.
  • stable ⁇ -titanium alloys are suitable for all alloy elements which have a stabilizing effect on the cubic, body-centered ⁇ phase.
  • alloy elements which have a stabilizing effect on the cubic, body-centered ⁇ phase.
  • These are V, Al, Fe, Ni, Co, Mn, Cr, Mo, Zr, Nb, Sn, Cu, which can be used both individually and in combination.
  • certain concentration limits can be specified which satisfy the above conditions, which can be derived from the thermodynamic equilibria.
  • Titanium alloys belonging to the binary type are particularly suitable and, in addition to titanium, also 14 to 20% by weight vanadium or 4 to 6% by weight iron or 6.5 to 9% by weight manganese or 13 to 19% by weight Contain molybdenum.
  • Further preferred alloys are those of the ternary type and, in addition to titanium, also 13 to 19% by weight vanadium plus 0.2 to 6% by weight aluminum or 4 to 6% by weight iron plus 0.2 to 6% by weight .-% aluminum or 1.5 to 2.3 wt .-% iron plus 10 to 14 wt .-% vanadium.
  • alloys which belong to the quaternary type and, in addition to titanium, also contain 9 to 11% by weight of vanadium plus 1.6 to 2.2% by weight of iron plus 2 to 4% by weight of aluminum.
  • the mechanically unstable / 3-titanium alloys defined and characterized above show three shape memory effects depending on the thermomechanical or mechanical pretreatment and depending on the temperature range. If tension is exerted on such an alloy by tension, pressure, shear or a combination of at least two of these operations in such a way that a primary permanent deformation is generated, the prerequisites for the setting of a memory effect are given.
  • tension is exerted on such an alloy by tension, pressure, shear or a combination of at least two of these operations in such a way that a primary permanent deformation is generated, the prerequisites for the setting of a memory effect are given.
  • the component By heating the component to a temperature above A S following the deformation, the one-way effect is initially established (see FIG. 3). With further heating up to AF , the effect that exists in a deformation opposite to the original direction of deformation has ended.
  • a S and A F give the temperature of the beginning or ending reconversion of the martensite into the high temperature phase.
  • the component undergoes a deformation which runs in the opposite direction to that of the one-way effect, and is therefore aligned with the originally applied permanent deformation.
  • this deformation with temperature takes place continuously and practically without hysteresis: the behavior of the material is therefore more similar to that of a bimetal.
  • the curve is not linear but slightly curved, so that it appears concave towards the temperature axis.
  • a S which has already been described in general terms above, is intended to be procedural in terms of this invention African size can be defined more precisely.
  • a S is to be understood as the temperature at which 1/100 of the previously applied primary permanent mechanical deformation is reduced.
  • a 90 which is characteristic of the memory effects, is to be introduced. This is to be understood as the temperature at which the structure of the component still contains a maximum of 10 vol.% Martensite after previous deformation and subsequent heating.
  • the workpiece must be heated to a temperature above A S after primary deformation.
  • the workpiece In the case of the isothermal effect, the workpiece must be heated to a temperature at which the stable ⁇ phase separates, and it must be kept at this temperature until at least 1 % by volume of the original phase has entered the ⁇ - Have converted phase.
  • the two-way effect If the two-way effect is to be used, the workpiece must be heated to a temperature above A 90 after primary deformation and then cooled to a temperature below A S.
  • the aforementioned conditions are the minimum conditions in order to achieve the said memory effects at all.
  • the optimal one-way effect is only obtained after heating to a temperature around A F.
  • the two-way effect can be achieved by heating to a temperature between A S and A F , the structure consisting partly of the aC "phase and partly of the ⁇ phase.
  • Beta titanium alloys are generally made by double-arc melting with an consumable electrode.
  • the starting material is titanium sponge and corresponding master alloys.
  • the melting process takes place under vacuum or protective gas with a low hydrogen partial pressure.
  • To produce a component the components are mixed, melted and cast, and the workpiece obtained in this way is thermoformed and subjected to solution annealing in the temperature range at least in part of the stable / 3 phase.
  • the workpiece is then quenched to room temperature and subjected to mechanical deformation and further thermal treatment.
  • Samples were made from the material in the delivery state, namely tensile samples according to FIG. 6, and hollow torsion samples according to FIG. 7.
  • the samples were in the area of the ⁇ phase 850 0 C solution annealed for 60 minutes and then quenched in moving water to room temperature.
  • the heat treatment was either carried out in a vacuum oven or the samples were placed in an airtightly sealed quartz glass ampoule filled with protective gas. The glass ampoule breaks immediately when immersed in the quenching medium (water), thus allowing rapid quenching. Both during heat treatment under vacuum and when using the protective gas-filled ampoule, the samples were additionally wrapped loosely in zirconium foil in order to bind residual oxygen due to its high affinity for zirconium.
  • Example II Tensile and torsion specimens were produced from the same material and according to the same method as given in Example I.
  • a tensile test was stressed at room temperature to produce a permanent set of 3.7%.
  • the sample initially showed a one-way effect, i.e. shrinkage occurred in the longitudinal axis (qualitatively similar to Fig. 3).
  • After cooling to room temperature there was an expansion in the longitudinal direction.
  • the sample was then cyclically heated and cooled a few times. The corresponding expansion or contraction between room temperature and approx. 340 ° C was 0.4% (two-way effect).
  • a torsion bar (see FIG. 7) was produced from Til0V2Fe3Al according to Example I.
  • Example I tensile specimens were machined from Til0V2Fe3Al and deformed as described therein and heated to 300 c 0th As expected, the one-way effect occurred in the form of a corresponding shrinkage in the longitudinal direction of the rod. The samples were then heated to a temperature of 400 to 450 ° C. and held at this temperature for 100 minutes. The test bars extended in the longitudinal direction from the values which were in the order of magnitude of 1 to 2%, depending on the primary deformation applied. This irreversible isothermal effect, which runs counter to the one-way effect, is shown qualitatively in FIG. 5. Elongation values from to rel. 50% (based on the primary permanent set applied) can be achieved.
  • a wire was produced from the material according to Example I and after the pretreatment specified there, and a coil spring 7 was wound therefrom. This spring was then subjected to a treatment according to Example II or III in order to bring about the two-way effect in such a way that the spring 7, which is in the idle state at room temperature under a slight compressive preload, contracts gradually as the temperature rises.
  • the spring 7 made of memory alloy was assembled in an electrical switch according to FIG. 8 together with an ordinary compression spring 8. The current is passed through the spring 8. In the normal state, it causes no heating, so that the latter is practically at room temperature and is in equilibrium with the counter spring 8.
  • a torsion bar according to FIG. 7 was produced from the material according to Example I and after the pretreatment specified there. The latter was treated further in accordance with Example II or III in order to produce the two-way effect.
  • the prepared torsion bar 10 was now provided with a switching arm 11 and mounted on the base plate 9. All other components of the electrical switch result from the description of FIG. 9.
  • the torsion bar 10 can be directly flowed through by the current (direct heating) or tightly enclosed by an insulated heating coil (indirect heating).
  • the trigger mechanism is basically the same as that given in Example I.
  • the counter spring is omitted here. This construction is characterized by great simplicity.
  • the trigger temperature can be set within wide limits by suitable selection of the switch geometry (length of the switching arm and swivel range etc.).
  • a hollow cylindrical sleeve 13 of 20.25 mm inside and 26.25 mm outside diameter with 30 mm axial length was produced from Til0V2Fe3Al. It served to two pipes 14 (metal, plastic, ceramic material) of 20.6 mm To connect outside diameter.
  • the sleeve 13 was pretreated according to Example I (solution annealing, quenching). Thereupon it was expanded by means of a polished steel ball 16 of 21 mm in diameter by axially pushing it through (see arrow in FIG. 11) to an inner diameter of 2.0.79 mm. Now the pipes 14 were inserted axially symmetrically into the sleeve and the whole thing was heated to a temperature at A F (in the present case approx. 260 ° C.).
  • the heating of the sleeve 13 made of titanium alloy can be accomplished in a simple manner in any workshop and also outdoors or at the assembly site by means of a blowtorch, welding torch, etc., whereby simple means (tarnishing colors, temperature chalks etc.) are sufficient for temperature monitoring.
  • the shrunk-on sleeve 17 (FIG. 12) is brought to a temperature of approx. AF plus 100 to 150 ° C., the irreversible isothermal memory effect occurring and the sleeve expanding (18 in FIG. 13). In this state, the tubes 14 can be pulled out of the sleeve 18. Should If the latter are used again, the process must be repeated from the beginning: solution annealing, quenching, pre-forming etc.
  • the component can optionally have at least one of the effects described above, for example the shape of a simple or offset leaf spring or the shape of any torsion bar and that of a cylindrical or conical coil spring.
  • connection or termination elements e.g. Hollow bodies
  • the components made of memory alloy can have a wide variety of shapes, of which FIGS. 14 to 17 show only a selection.
  • the component can have the shape of a simple or stepped cylindrical, square, hexagonal or octagonal hollow body.
  • the component can be designed as a solid or perforated cylindrical or polygonal disc provided with a bead on one or both sides.
  • the components made of mechanically unstable j.9 titanium alloy can be used, for example, as temperature-dependent triggering elements in electrical switches, as temperature sensors in general, as fixed or detachable connecting sleeves for pipes and rods, and as fixed or detachable seals (disk or socket shape) for ceramic components.
  • Beta titanium alloys are also characterized by good hot and cold formability and machinability.
  • Til0V2Fe3Al there is also a commercially available alloy, which means significant economic advantages over previous conventional memory alloys based on another alloy.

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  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
  • Materials For Medical Uses (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
EP82200313A 1981-03-23 1982-03-11 Procédé de fabrication d'un élément de construction en un alliage à base de titane, ainsi que l'élément et son application Expired EP0062365B1 (fr)

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CH1934/81 1981-03-23
CH193481 1981-03-23

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EP0062365A1 true EP0062365A1 (fr) 1982-10-13
EP0062365B1 EP0062365B1 (fr) 1984-12-27

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US (1) US4412872A (fr)
EP (1) EP0062365B1 (fr)
JP (1) JPS57185965A (fr)
DE (1) DE3261668D1 (fr)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0110685A1 (fr) * 1982-11-30 1984-06-13 Beta Phase Inc. Dispositif à régulation de débit intraveineux employant un élément à mémoire de forme pour le contrôle de l'écoulement
EP0143580A1 (fr) * 1983-11-15 1985-06-05 RAYCHEM CORPORATION (a Delaware corporation) Alliages à mémoire de forme
US4645489A (en) * 1982-11-30 1987-02-24 Beta Phase, Inc. Fluid delivery apparatus with shape-memory flow control element
EP0246828A1 (fr) * 1986-05-18 1987-11-25 Daido Tokushuko Kabushiki Kaisha Objets en titanium ou en alliage de titanium résistant à l'usure
US4713063A (en) * 1985-04-29 1987-12-15 Beta Phase, Inc. Intravenous tube and controller therefor
US4731069A (en) * 1986-05-01 1988-03-15 Beta Phase, Inc. Intravenous tube and controller therefor
FR2694696A1 (fr) * 1992-08-14 1994-02-18 Memometal Ind Pièce contentive pour ostéosynthèse, notamment agrafe, en alliage à transition austénite/martensite proche de la température ambiante.

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JPS59230189A (ja) * 1983-06-13 1984-12-24 松下電器産業株式会社 熱感応装置
US4654092A (en) * 1983-11-15 1987-03-31 Raychem Corporation Nickel-titanium-base shape-memory alloy composite structure
US4895438A (en) * 1983-12-06 1990-01-23 Cvi/Beta Ventures, Inc. Eyeglass frame including shape-memory elements
US4896955B1 (en) * 1983-12-06 1991-05-21 Eyeglass frame including shape-memory elements
US4772112A (en) * 1984-11-30 1988-09-20 Cvi/Beta Ventures, Inc. Eyeglass frame including shape-memory elements
US4617448A (en) * 1984-12-18 1986-10-14 North American Philips Corporation Electrically releasable locking device
JPS61185720A (ja) * 1985-02-13 1986-08-19 Sasaki Gankyo Kk 眼鏡の可調整型超弾性パツドア−ム
EP0192475A3 (fr) * 1985-02-20 1987-02-04 Sampson, Ronald Spencer Activeur automatique de fermeture
US4616499A (en) * 1985-10-17 1986-10-14 Lockheed Corporation Isothermal forging method
GB2209200A (en) * 1987-08-28 1989-05-04 Thorn Emi Flow Measurement Ltd Thermal cut-off valve
JPH01155245U (fr) * 1988-04-14 1989-10-25
US5114504A (en) * 1990-11-05 1992-05-19 Johnson Service Company High transformation temperature shape memory alloy
US5344506A (en) * 1991-10-23 1994-09-06 Martin Marietta Corporation Shape memory metal actuator and cable cutter
US5312152A (en) * 1991-10-23 1994-05-17 Martin Marietta Corporation Shape memory metal actuated separation device
US5226979A (en) * 1992-04-06 1993-07-13 Johnson Service Company Apparatus including a shape memory actuating element made from tubing and a means of heating
FR2703184B1 (fr) * 1993-03-03 1995-12-01 Gen Electric Contacteur actionné électro-thermiquement.
US6149742A (en) * 1998-05-26 2000-11-21 Lockheed Martin Corporation Process for conditioning shape memory alloys
US6548013B2 (en) 2001-01-24 2003-04-15 Scimed Life Systems, Inc. Processing of particulate Ni-Ti alloy to achieve desired shape and properties
US7700038B2 (en) * 2005-03-21 2010-04-20 Ati Properties, Inc. Formed articles including master alloy, and methods of making and using the same
JP2008075173A (ja) * 2006-01-18 2008-04-03 Nissan Motor Co Ltd 低ヤング率チタン合金
US7670445B2 (en) * 2006-01-18 2010-03-02 Nissan Motor Co., Ltd. Titanium alloy of low Young's modulus
JP5831283B2 (ja) * 2012-02-17 2015-12-09 新日鐵住金株式会社 熱処理により加工方向と同一方向への形状変形するチタン合金部材とその製造方法
US11185608B2 (en) * 2018-08-09 2021-11-30 Cook Medical Technologies Llc Method of treating a superelastic medical device to improve fatigue life
CN113293324B (zh) * 2021-05-12 2022-05-10 东南大学 具有高使用温度的可调控热膨胀系数的钛铌钼合金及其制备方法和应用

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US3652969A (en) * 1969-05-27 1972-03-28 Robertshaw Controls Co Method and apparatus for stabilizing and employing temperature sensitive materials exhibiting martensitic transitions
US3748197A (en) * 1969-05-27 1973-07-24 Robertshaw Controls Co Method for stabilizing and employing temperature sensitive material exhibiting martensitic transistions
FR2301602A1 (fr) * 1975-02-18 1976-09-17 Raychem Corp Preconditionnement mecanique d'alliages metalliques

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CH616270A5 (fr) * 1977-05-06 1980-03-14 Bbc Brown Boveri & Cie

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US3652969A (en) * 1969-05-27 1972-03-28 Robertshaw Controls Co Method and apparatus for stabilizing and employing temperature sensitive materials exhibiting martensitic transitions
US3748197A (en) * 1969-05-27 1973-07-24 Robertshaw Controls Co Method for stabilizing and employing temperature sensitive material exhibiting martensitic transistions
FR2301602A1 (fr) * 1975-02-18 1976-09-17 Raychem Corp Preconditionnement mecanique d'alliages metalliques

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0110685A1 (fr) * 1982-11-30 1984-06-13 Beta Phase Inc. Dispositif à régulation de débit intraveineux employant un élément à mémoire de forme pour le contrôle de l'écoulement
US4645489A (en) * 1982-11-30 1987-02-24 Beta Phase, Inc. Fluid delivery apparatus with shape-memory flow control element
EP0143580A1 (fr) * 1983-11-15 1985-06-05 RAYCHEM CORPORATION (a Delaware corporation) Alliages à mémoire de forme
US4713063A (en) * 1985-04-29 1987-12-15 Beta Phase, Inc. Intravenous tube and controller therefor
US4731069A (en) * 1986-05-01 1988-03-15 Beta Phase, Inc. Intravenous tube and controller therefor
EP0246828A1 (fr) * 1986-05-18 1987-11-25 Daido Tokushuko Kabushiki Kaisha Objets en titanium ou en alliage de titanium résistant à l'usure
US4902359A (en) * 1986-05-18 1990-02-20 Daido Tokushuko Kabushiki Kaisha Wear-resistant titanium or titanium-alloy member and a method for manufacturing the same
FR2694696A1 (fr) * 1992-08-14 1994-02-18 Memometal Ind Pièce contentive pour ostéosynthèse, notamment agrafe, en alliage à transition austénite/martensite proche de la température ambiante.

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US4412872A (en) 1983-11-01
JPS6349741B2 (fr) 1988-10-05
EP0062365B1 (fr) 1984-12-27
DE3261668D1 (en) 1985-02-07
JPS57185965A (en) 1982-11-16

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