US3783037A - Treatment of alloys - Google Patents

Treatment of alloys Download PDF

Info

Publication number
US3783037A
US3783037A US00088596A US3783037DA US3783037A US 3783037 A US3783037 A US 3783037A US 00088596 A US00088596 A US 00088596A US 3783037D A US3783037D A US 3783037DA US 3783037 A US3783037 A US 3783037A
Authority
US
United States
Prior art keywords
alloy
temperature
alloys
shape
deformation
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.)
Expired - Lifetime
Application number
US00088596A
Other languages
English (en)
Inventor
G Brook
R Iles
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Fulmer Research Institute Ltd
Original Assignee
Fulmer Research Institute Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Fulmer Research Institute Ltd filed Critical Fulmer Research Institute Ltd
Application granted granted Critical
Publication of US3783037A publication Critical patent/US3783037A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C5/00—Alloys based on noble metals
    • C22C5/02—Alloys based on gold
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C5/00—Alloys based on noble metals
    • C22C5/04—Alloys based on a platinum group metal
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C5/00—Alloys based on noble metals
    • C22C5/06—Alloys based on silver
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C5/00—Alloys based on noble metals
    • C22C5/06—Alloys based on silver
    • C22C5/10—Alloys based on silver with cadmium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/01—Alloys based on copper with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/05—Alloys based on copper with manganese as the next major constituent

Definitions

  • This invention is concerned with methods of treating alloys.
  • a method of making a heat-recoverable article comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy comprising an intermetallic compound Which on cooling from said first temperature undergoes a shear transformation to a banded martensite or which retains its first temperature structure or a related ordered structure as cooled from said first temperature but transforms into a banded martensite by shear on working in the cooled condition in such a way that the transformation is not fully reversible by unloading and which in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperatures and rate of cooling being such that on reheating the article at least partly, resumes its first shape.
  • the alloy contains at least 50% by weight of copper in the form of an intermetallic compound and said martensite has pseudo-cubic symmetry.
  • said rate 3,783,037 Patented Jan. 1, 1974 of cooling and lower temperature are such that the alloy has undergone (preferably fully, but in some cases partially) a shear transformation to a banded martensite before being plastically deformed into said second shape.
  • the alloy is plastically deformed into the second shape at or below the temperature at which the martensite transformation starts in the absence of externally applied stress (the M temperature) and preferably below the temperature at which the martensite transformation is completed in the absence of externally applied stress (the M temperature).
  • the A, temperature On reheating above a certain temperature (the A, temperature), the alloy will start to transform back to the high temperature phase and this transformation will be accompanied by a change in shape towards said first shape. Above a certain temperature (the A; temperature), the transformation to the high temperature phase will be complete.
  • said rate of cooling and lower temperature are such that the alloy retains its first temperature structure or a related ordered structure at said lower temperature and the plastic deformation into said second shape causes a shear transformation into a banded martensite.
  • the alloy in its stable (5) or metastable high temperature phase is plastically deformed into the second shape above the M temperature.
  • the application of the deforming stress produces a martensite similar to that obtained by cooling below the M temperature.
  • the stressinduced martensite transforms back to the original high temperature phase and the alloy changes in shape towards said first shape.
  • the alloy may be cooled further below the M (and preferably below the M temperature, with or without the application of external stress.
  • the transformation into martensite (if not already completed by the application of the deforming stress) will continue with a further change in shape in the direction dictated by said deforming stress.
  • On reheating above the A temperature the shape will change towards the first shape.
  • the amount of heat-recoverable strain is greater when the plastic deformation is elfected at temperatures closer to the M and M; temperatures.
  • the copper-containing intermetallic compounds which give the best results are those in which the high temperature body centred cubic phase of A2 structure transforms on rapid cooling ultimately to a martensite which, though of complex crystal structure such as an orthorhombic structure, has pseudo-cubic symmetry.
  • Such martensites are characterized by having a metallographic structure containing high densities of stacking faults. Alloys with this structure can be readily deformed at and near the M and F temperatures with extensive ductility as will be described hereinafter.
  • Such an alloy may be found, for example, in the copper-zinc system where the B phase of appropriate composition of A2 BCC structure first orders to a B2 (CsCl type) BCC structure which subsequently transforms on further cooling to a faulted martensite of pseudo-cubic symmetry.
  • Another example may be found in the copper-aluminium system where the structure of the final martensite is dependent on composition.
  • An alloy with 10-11% aluminium does not order before transforming to a faulted martensite of pseudo-cubic symmetry.
  • An alloy with 11 to 13% aluminium first orders to a BCC (Fe Al type) structure based on the theoretical composition Cu Al before subsequent transformation to a faulted martensite of pseudo-cubic symmetry.
  • the alloys preferably used in the present invention are those which transform martenstically to a faulted martensite of pseudo-cubic symmetry.
  • Such structures may be found, for example, in a binary copper-zinc alloy, a binary copper-aluminium alloy, a ternary copper-aluminium-zinc alloy, a ternary copper-zinc-tin alloy, a ternary copper-zinc-silicon alloy, a ternary copper-zinc-manganese alloy, a ternary copper-aluminium-iron alloy and a ternary copper-aluminium-nickel alloy.
  • the alloy may of course contain impurities and/or other incidental elements included to modify the properties of the alloy provided that an intermetallic compound of copper exhibiting the required martensite transformation is maintained, and the alloy is not necessarily a binary or ternary alloy.
  • the alloy may be a two-phase or multi-phase alloy in which at last one phase is an intermetallic compound of copper as hereinbefore defined.
  • the other phase or at least one of the other phases may consist of a primary solid solution which is heat-recoverable as described in our co-pending patent applictaion No. 55,481/69.
  • a primary solid solution as meant in this specification is obtained when atoms of one or more different elements can be added to a pure metal without producing a change of crystal structure, by replacing atoms in the various sites of the pure metal crystal structure.
  • An intermetallic compound as meant in this specification is the single phase produced, other than a primary solid solution, when two or more elements are alloyed together in the correct proportions. It usually has a crystal structure different from that of any of the pure elements and usually includes a composition corresponding to a simple ratio of atoms e.g. A B where A and B are elements and x and y are numbers usually below 10. It includes such phases which also exhibit a range of solubility for the component elements around the simple atomic ratio without a change of crystal structure.
  • FIGS. 7 and 8 show the stress/strain curves shown in FIGS. 7 and 8.
  • FIG. 7 shows the behavior of many of the alloys found on deformation below M; temperature and
  • FIG. 8 shows the behavior of many of the alloys found on deformation between M and M temperatures.
  • FIG. 9 shows the behavior of many of the alloys on deformation as indicated in FIG. 9.
  • alloys used in this invention have high internal frictions or damping capacities when heattreated in the manner described i.e. cooled from the appropriate temperature in such a manner that they undergo the martensitic transformation.
  • This internal friction or damping capacity reaches its highest value at temperatures near to the M anw F temperatures.
  • One method is to suppress or partially suppress the shape change by an applied stress and then to use the force or energy released when the restraining force is removed suddenly to operate a device, for example, through a level or by impact on a pin or by deforming or fracturing a suitable element of the device.
  • Another method to use the force developed is to heat the part made from the heat recoverable material slowly through the A A, temperature range when it will exert a sustained and progressively increasing force on the operating element of the device as mentioned before. By control of the temperature, the rate and amount of increase of force or of movement can be controlled.
  • Said strain may be applied by deforming the alloy in its high-temperature phase partly towards the shape required for the low-temperature phase, the temperature being subsequently lowered so that the alloy changes into its low-temperature phase.
  • the change into the lowtemperature phase is accompanied by a continued change of shape into the desired shape without the application of an external force.
  • This form of the invention is of great practical value since it provides a means of putting an alloy at a comparatively high temperature into a condition in which it will deform spontaneously at lower temperatures to a new shape which is dictated by the initial high temperature deformation. It is therefore unnecessary to effect working of the alloy at low temperatures.
  • the metastable high temperature phase of the alloy is cooled to between its M and M transformation temperatures.
  • M is the temperature of the start of the martensitic transformation under stress and M is the temperature of the start of the transformation without applied stress.
  • the temperature should be as close to the M transformation temperature as possible, e.g. within 10 C., to obtain the desired residual internal stress by said partial deformation. In other alloys a greater margin of temperature above M is possible.
  • a suitable temperature for a given alloy can readily be found by experiment.
  • the alloy is then deformed a small amount (i.e. less than the final strain it is desired to put into the low temperature phase). Cooling is continued to below the M transformation temperature when the alloy will continue to change in shape in the direction indicated by the prior deformation. On reheating this change of shape is wholly or partly reversed and on cooling again the change in shape towards the low temperature shape occurs spontaneously. Continued heating alrlid cooling is accompanied by continued changes in s ape.
  • the alloy is deformed into a desired shape in its low-temperature phase and said strain is applied by raising the temperature so that the alloy changes into its high-temperature phase while restraint is applied to the alloy to prevent a change in shape.
  • a method of making a heat-recoverable article from a heat-recoverable alloy which method includes the steps of shaping the alloy at an elevated temperature into a first shape, cooling to a lower temperature, deforming the alloy at the lower temperature into a second shape, said temperatures being such that if reheated without restraint to an appropriate temperature the alloy would at least partly resume its first shape, and reheating the alloy to said appropriate temperature while subjecting it to restraint which prevents a change of shape.
  • the alloy may be cooled to the lower temperature after reheating, still retaining the second shape. Then if the alloy is reheated without restraint it will change wholly or partly to its first shape but on cooling will revert wholly or partly to its second shape. Continued heating and cooling is accompanied by continued changes in shape.
  • Reheating under restraint is particularly useful since it enables the upper temperature to which the alloy is heated to be so far above the transformation temperature that continued reversibility of shape would be lost in the absence of restraint. Nevertheless, the upper temperature must not be suflicient for relaxation of stress to occur by plastic deformation, e.g. creep, or reversibility will be lost.
  • the temperature to which the alloy is heated should be too low for ageing or tempering of the alloy to take place. If precipitation occurs, the alloy assumes its high temperature shape permanently.
  • the restraint need not always be applied by external mechanical means such as a jig.
  • an oxide skin, a metal coating or the like can provide the necessary restraint.
  • alloys normally have an u+fi phase structure if cooled slowly to room temperature. To obtain heat recoverable properties the alloys must be quenched from at least 870 C. to retain a 13 phase which will transform martensitically when cooled below room temperature.
  • each alloy was bent to a 60 bend from its original position at a temperature just below its M and heated above the A All of the alloys recovered very closely to their original straight position (within -5 the temperature of the start of recovery corresponding very closely to the A temperature. In these alloys, the amount of heat recoverable strain was less dependent on the deformation temperature below the M than in the case of the Cu-Zn binary alloys, and in fact, recovery was obtained from an alloy with an M of +320 C. after deformation at +20 C.
  • the amount of recovery is extremely small, and in practice the temperature should be close to the M When deforming above the M alloys which have an M greater than 0., care must be taken since at these temperatures decomposition of the 3 phase may take place to an extent that the residual ,6 phase has a much lower M temperature.
  • the M of alloy 507 was -50 C. and of alloy 508 l0 C. and of alloy 510 +50 C.
  • Alloys 493, 507, 508 and 510 all had their M temperature below 100 C. A number of experiments were performed upon alloys whose M was above 100 C. Examples of the results obtained from these experiments will be given for three of those alloys tested; namely alloys 483, 484, and 485. The nominal compositions of these alloys is given below:
  • All alloys within this composition range exhibit heat recoverable properties when heated above their A after deformation at temperatures either above or below the M,.
  • the alloys in this ternary system had similar characteristics to those in the Cu-Al-Zn system in that the yield stress was a minimum and the ductility (i.e. total strain at fracture) a maximum when the material was deformed at its M Ductility decreased as tin replaced zinc.
  • alloy 488 One of the alloys in this system which were tested (alloy 488) had a composition 63.85 wt. percent Cu, 31.25 wt. percent Zn, 4.9 wt. percent Sn; this alloy had an M of 7'0 C.
  • One new phenomenon that was observed during the testing of this alloy was what may be termed as reverse heat-recoverable strain; this was the first time that this effect had been found.
  • Alloy 488 was also used to illustrate the phenomena of suppression of recovery by heating under restraint. Samples were deformed 2.8% in tension at 80 C. and were then loaded to stresses up to 30,000 lb.,/in. On heating to ambient temperature, the amount of heat recoverable strain was found to decrease with increasing l Nominal.
  • All alloys within this composition range exhibit heat recoverable properties when heated above their A after deformation at temperatures either above or below the M
  • alloys within the composition range AFGDE to exhibit heat recoverable properties, they must be quenched from not below 825 C.
  • Alloys within the range BCGF must be quenched from not below 850 C.
  • the alloys in this ternary system had similar characteristics to those in the two ternary systems which were previously described in that the yield stress was a minimum and the ductility a maximum when the material was deformed between M and M:-
  • Alloy 521 which had a nominal composition 63.75 wt. percent Cu, 34.5 wt. percent Zn, 1.75 wt. percent Si and an M of -140 C., gave results shown in Table XI.
  • Alloy 515 which had a nominal composition 66.5 wt. percent Cu, 31.25 wt. percent Zn, 2.25 wt. percent Si and an M of 50 C., gave results shown in Table XII.
  • Alloy 522 which had a nominal composition 69.25 wt. percent Cu, 27.5 wt. percent Zn, 3.25 wt. percent Si and M of +75 0., gave results shown in Table XIII.
  • Alloy 521 also illustrates the elfect of heating under a restraining stress. Samples were deformed 4.8% in tension at -196 C. They were then heated to ambient temperature under various stresses up to 35,000 lb. /in. and the amount of strain recovered measured. One sample was stressed to 40,000 lb. /in. which is above the yield stress of the high temperature phase. This sample extended rapidly just above the A temperature. Since the specimens were dead-loaded, this caused rapid extension and ultimate failure. Results are shown in Table XIV.
  • alloys within this composition field are preferably quenched from not below 900 C. into water.
  • the alloys in this ternary system had similar characteristics to those described in the previous ternary systems in that the yield stress was a minimum and the ductility a maximum when the material was deformed between M and M; temperatures.
  • Alloy 992 had an M of +240 C., 993 an M of +160 C., and 994 an M of +100 C.
  • alloys within this field are preferably quenched from not below 900 C. into water.
  • the alloys in this ternary system had similar characteristics to those alloys previously described in that the yield stress was a minimum and the ductility a maximum when the material was deformed between its M and M, temperatures.
  • Alloy 989 has an M of ;+300 C., 990 an M, of +250 C., and 991 an M of +250 C.
  • Wt. percent Wt. percent (vii) Ternary copper-aluminum-iron alloys (A) 87.0, Cu; 13.0, Al (B) 90.0, Cu; 10.0, Al (C) 84.0, Cu; 11.0, Al; 5.0, Ni (D) 81.25, Cu; 13.75, A1; 5.0, Ni
  • alloys within this field are preferably quenched from not below 950 C. into water.
  • Alloys within this composition field have relatively low ductility unless deformed at very low temperatures e.g. -196 C.; however, they do exhibit heat recoverable properties after deformation either above or below the M
  • An example of an alloy in this composition field is one containing 84 wt. percent Cu, 2.75 wt. percent Ni, 13.25 wt. percent Al; this alloy has an M of +82 C.
  • heat recoverable properties were exhibited by this alloy after deformation in the temperature range --196 C. to C.
  • temperature and at 196 C. was any significant plastic deformation produced.
  • alloys used in the present invention are permanently deformed just above their M on quenching through the M the material tends to move in the direction of the applied deformation.
  • the duplex structure could be either (a+fi) or (y-I-fl). Alloys with the +0) structure were extremely brittle, this embrittlement being due to the precipitation of the 7 phase. Consequently, it is not possible for alloys with this type of microstructure to exhibit heat recoverable properties simply because it is extremely difficult to deform them. Since the or phase is a Cu rich phase, precipitation of this phase depletes the 5 matrix in Cu, and as a result the M of the alloy is decreased.
  • An example of this is an alloy of composition 66 wt. percent Cu, 32.25 wt. percent Zn, 1.75 wt. percent Al.
  • the alloy was quenched from 900 C., it was single phase and had an M of +10 C.
  • the structure was duplex (ct-H3) and as a result the M was depressed to 70 C.
  • the a phase which constituted 50% of the structure was discontinuous and globular in form. This two phase was deformed 3.4% at --78 C. (i.e. just below the M upon heating above the A 2.8% of this deformation was recovered.
  • the Cu-Zn-Sn alloy studied was 488 which in the single phase condition had an M of 70 C.
  • the microstructure of the alloy consisted of a B matrixcontaining a regular distribution of the a phase in the form of globules dispersed regularly throughout the matrix.
  • the a phase constituted approximately 40% of the structure and as a result the M was depressed to C.
  • This alloy was deformed over a range of temperatures; the results are summarized below in Table XVIII.
  • the M may be varied simply by altering the amount of second phase present.
  • the alloys may also contain impurities and incidental 17 constituents.
  • Mn and Fe may be added to Cu-Zn alloys
  • Sn and Si may be added to Cu-Al alloys, or to more complex alloys containing those elements. It is of course always necessary that the alloy has a composition such that heat-recovery as hereinbefore described is obtained.
  • the heat-recoverable properties possessed by articles made in accordance with the present invention render them useful for many purposes where a change of shape of temperature is necessary.
  • they may be used as tubes in couplings, which tubes change shape to grip two elements to be connected together, as temperature-responsive devices'in switching devices and as springs.
  • a method of making a heat-recoverable articl which method comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy comprising an intermetallic compound of copper which compound undergoes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method according to claim 13 including the step of raising the temperature of the alloy after it has been deformed into said second shape so that it changes shape towards said first shape.
  • a method of making a heat-recoverable article comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy comprising an intermetallic compound of silver which compound undergoes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a gold-aluminium intermetallic compound containing not more than 4% by weight of aluminium which compound under-goes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article which method comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a gold-indium intermetallic compound containing not more than 12% by weight of indium which compound undergoes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a gold-magnesium intermetallic compound containing not more than 15% by weight of magnesium which compound undergoes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article which method comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said 19 alloy consisting of a gold-manganese intermetallic compound containing not more than 38% by weight of manganese which compound undergoes a shear transformation to a banded martensite and which compound'in' 'the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforrriing the alloy into a second shape'a't the lower temperature, the temperature and rate of cooling being such thaton reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article which method comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a gold-zinc intermetallic compound containing not more than 30% by weight of zinc which compound undergoes a shear transformation to a banded martensite and whichcompound in the cooled condition has an anomalously low modulus of elasticity during load;- ing, and then plasti'cally deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shapel' 25.
  • a method of making a heat-recoverable article comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a gold-copper intermetallic compound containing not more than 80% by weight of gold which compound undergoes a shear transformation to a banded martensite and which compound in the cooled condition has an anomalously low modulus of elasticity during loading, and then plastically deforming the alloy into a second shape at the lower temperature, the temperature and rate of cooling being such that on reheating the article at least partly resumes its first shape.
  • a method of making a heat-recoverable article which method comprises cooling an alloy in a first shape from a first temperature to a lower temperature, said alloy consisting of a cobalt-platinum-intermetallic comfrom a fi'r's't temperature to a lower temperature, said alloy.
  • Apparatus including a heat-recoverable article according to claim 28, the article performing a function in said apparatus by virtue ofits property of changing shape with temperature.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Adornments (AREA)
  • Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
US00088596A 1969-11-12 1970-11-12 Treatment of alloys Expired - Lifetime US3783037A (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
GB5548269 1969-11-12
GB5596969 1969-11-14

Publications (1)

Publication Number Publication Date
US3783037A true US3783037A (en) 1974-01-01

Family

ID=26267558

Family Applications (2)

Application Number Title Priority Date Filing Date
US00088596A Expired - Lifetime US3783037A (en) 1969-11-12 1970-11-12 Treatment of alloys
US05/607,553 Expired - Lifetime USRE31474E (en) 1969-11-12 1975-08-25 Treatment of alloys

Family Applications After (1)

Application Number Title Priority Date Filing Date
US05/607,553 Expired - Lifetime USRE31474E (en) 1969-11-12 1975-08-25 Treatment of alloys

Country Status (11)

Country Link
US (2) US3783037A (xx)
JP (1) JPS5511740B1 (xx)
BE (1) BE758862A (xx)
BR (1) BR7023837D0 (xx)
CA (1) CA970670A (xx)
CH (1) CH580167A5 (xx)
DE (1) DE2055755C2 (xx)
FR (1) FR2067253B1 (xx)
IL (1) IL35632A (xx)
NL (1) NL172766C (xx)
SE (1) SE389690B (xx)

Cited By (34)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2516749A1 (de) * 1974-05-04 1975-11-20 Univ Osaka Metallkoerper mit reversiblem gestaltwechselvermoegen und verfahren zu deren herstellung
US3977913A (en) * 1972-12-01 1976-08-31 Essex International Wrought brass alloy
US4014716A (en) * 1971-01-18 1977-03-29 Essex International, Inc. Wrought brass alloy having a low spring back coefficient and shape memory effect
US4036669A (en) * 1975-02-18 1977-07-19 Raychem Corporation Mechanical preconditioning method
US4055445A (en) * 1974-09-20 1977-10-25 Essex International, Inc. Method for fabrication of brass alloy
US4067752A (en) * 1973-11-19 1978-01-10 Raychem Corporation Austenitic aging of metallic compositions
US4095999A (en) * 1972-11-17 1978-06-20 Raychem Corporation Heat-treating method
US4099991A (en) * 1974-10-10 1978-07-11 Essex Group Method for effecting reverse shape memory phenomena in Cu-Zn-Si brass alloy
US4113475A (en) * 1976-04-09 1978-09-12 Kennecott Copper Corporation Tarnish resistant copper alloy
US4144104A (en) * 1976-03-18 1979-03-13 Raychem Corporation Stable heat shrinkable ternary β-brass alloys containing aluminum
US4146392A (en) * 1976-03-18 1979-03-27 Raychem Corporation Stable heat shrinkable ternary beta-brass type alloys containing manganese
DE2900518A1 (de) * 1978-01-09 1979-07-19 Raychem Sa Nv Verfahren zur bildung einer dichten abzweigenden verbindung und zur durchfuehrung des verfahrens bestimmte klammer
US4166739A (en) * 1976-03-18 1979-09-04 Raychem Corporation Quarternary β-brass type alloys capable of being rendered heat recoverable
US4274872A (en) * 1978-08-10 1981-06-23 Bbc Brown, Boveri & Company Brazable shape memory alloys
US4285739A (en) * 1977-12-28 1981-08-25 Leuven Research And Development Vzw Process of manufacturing solid bodies of copper-zinc-aluminium alloys
EP0035070A1 (de) * 1980-03-03 1981-09-09 BBC Aktiengesellschaft Brown, Boveri & Cie. Gedächtnislegierung auf der Basis eines kupferreichen oder nickelreichen Mischkristalls
EP0035601A1 (de) * 1980-03-03 1981-09-16 BBC Aktiengesellschaft Brown, Boveri & Cie. Verfahren zur Herstellung einer Gedächtnislegierung
EP0035602A1 (de) * 1980-03-03 1981-09-16 BBC Aktiengesellschaft Brown, Boveri & Cie. Verfahren zur pulvermetallurgischen Herstellung einer Gedächtnislegierung auf der Basis von Kupfer, Zink und Aluminium
JPS56136945A (en) * 1980-03-03 1981-10-26 Bbc Brown Boveri & Cie Shaped memory alloy based on cu al or cu al ni and stabilization of said alloy in two-direction effect
US4296955A (en) * 1975-04-09 1981-10-27 Raychem Corporation Composite coupling device with high recovery driver
JPS57175640A (en) * 1981-04-21 1982-10-28 Matsushita Electric Ind Co Ltd Roller unit
US4448824A (en) * 1982-01-28 1984-05-15 Raychem Corporation Wraparound protective closure
US4621844A (en) * 1982-01-25 1986-11-11 Shell Oil Company Memory metal connector
US4781606A (en) * 1980-12-12 1988-11-01 Raychem Corporation Wire stripping arrangement
US4832382A (en) * 1987-02-19 1989-05-23 Raychem Corporation Coupling device
DK156254B (da) * 1975-02-18 1989-07-17 Raychem Corp Fremgangsmaade til fremstilling af en varme-restituerbar genstand af et metalmateriale, der kan undergaa reversibel omdannelse mellem en austenitisk og en martensitisk tilstand
US4872713A (en) * 1987-02-19 1989-10-10 Raychem Corporation Coupling device
US5002716A (en) * 1984-11-14 1991-03-26 Raychem Corporation Joining insulated elongate conduit members
US5362141A (en) * 1990-04-27 1994-11-08 Alfred Teves Gmbh Valve block and method of assembling an element thereto
DE2954743C2 (de) * 1978-01-09 1996-10-31 Raychem Sa Nv Verfahren zur Bildung einer dichten Verbindung zwischen einer wärmegeschrumpften Muffe und wenigstens zwei langgestreckten, vom gleichen Ende in die Muffe eintretenden Substraten
WO2003035918A2 (en) * 2001-10-22 2003-05-01 Council Of Scientific And Industrial Research Cu-zn-al(6%) shape memory alloy with low martensitic temperature and its process
US20090065103A1 (en) * 2007-09-10 2009-03-12 Sippola Pertti J Method and apparatus for improved formability of galvanized steel having high tensile strength
CN105063427A (zh) * 2015-08-28 2015-11-18 中国科学院金属研究所 一种磁兼容锌合金及其应用
US10160063B2 (en) * 2014-11-18 2018-12-25 Baker Hughes Incorporated Braze materials and earth-boring tools comprising braze materials

Families Citing this family (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2603878A1 (de) * 1975-02-18 1976-08-26 Raychem Corp Waermerueckstellbarer gegenstand aus einer metallischen zusammensetzung mit einer erweiterten martensitisch-austenitischen hystereseschleife und verfahren zu seiner herstellung
IT1054827B (it) * 1975-02-18 1981-11-30 Raychem Corp Metodo per il trattamento di composizioni metalliche e composizioni cosi ottenute
FR2344639A1 (fr) * 1976-03-18 1977-10-14 Raychem Corp Nouveaux alliages aptes a la reprise thermique
US4300284A (en) * 1978-12-15 1981-11-17 Raychem Corporation Method and apparatus to organize and to electrically connect wires
EP0045985B1 (de) * 1980-08-07 1984-02-08 BBC Aktiengesellschaft Brown, Boveri & Cie. Verfahren zur Herstellung einer Kupferbasis-Gedächtnislegierung
CH659482A5 (de) * 1982-02-05 1987-01-30 Bbc Brown Boveri & Cie Verfahren zur erzeugung eines reversiblen zweiweg-gedaechtniseffekts in einem bauteil aus einer einen einwegeffekt zeigenden legierung.
DE3370828D1 (en) * 1982-05-13 1987-05-14 Leuven Res & Dev Vzw Process for thermally treating heat recoverable metallic articles and articles thereby obtained
NL8201985A (nl) * 1982-05-13 1983-12-01 Leuven Res & Dev Vzw Werkwijze voor het dempen van trillingen gebruikmakend van voorwerpen uit een legering met vormgeheugen.
FR2589167A1 (fr) * 1985-10-28 1987-04-30 Boulanger Catherine Procede d'obtention d'objets metalliques dont la forme se modifie par chauffage, et objets obtenus par ce procede
JPH05222471A (ja) * 1991-12-16 1993-08-31 Toshiba Corp 装飾用銅鉄合金
ZA932674B (en) * 1992-05-06 1995-03-16 Mintek The aesthetic enhancement or modification of articles or components made of non-ferrous metals.
AU3783295A (en) * 1994-11-16 1996-05-23 Advanced Cardiovascular Systems Inc. Shape memory locking mechanism for intravascular stent
KR100701645B1 (ko) * 2004-08-02 2007-03-30 도레이새한 주식회사 연성회로기판용 적층구조체의 제조방법
DE102005035709A1 (de) * 2005-07-27 2007-02-15 Technische Universität Clausthal Kupferlegierung mit hoher Dämpfungskapazität und Verfahren zu ihrer Herstellung

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3012882A (en) * 1960-01-26 1961-12-12 Muldawer Leonard Temperature responsive cadmium-silver-gold alloys
US3374123A (en) * 1964-03-04 1968-03-19 Foundation Method of manufacturing non-magnetic, elastic articles having a small change of vibration and deflection for temperature change
US3351463A (en) * 1965-08-20 1967-11-07 Alexander G Rozner High strength nickel-base alloys
DE1558715B2 (de) * 1966-09-09 1972-05-31 Buehler William J Legierungen mit martensitischem uebergang
US3347717A (en) * 1966-10-04 1967-10-17 Olin Mathieson High strength aluminum-bronze alloy
FR1535373A (fr) * 1967-09-01 1968-08-02 Alliage à température de transition variable
US3567523A (en) * 1968-09-27 1971-03-02 Dow Chemical Co Pseudo-plastic behavior of uraniumniobium alloys
US3558369A (en) * 1969-06-12 1971-01-26 Us Navy Method of treating variable transition temperature alloys

Cited By (43)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4014716A (en) * 1971-01-18 1977-03-29 Essex International, Inc. Wrought brass alloy having a low spring back coefficient and shape memory effect
US4095999A (en) * 1972-11-17 1978-06-20 Raychem Corporation Heat-treating method
US3977913A (en) * 1972-12-01 1976-08-31 Essex International Wrought brass alloy
US4067752A (en) * 1973-11-19 1978-01-10 Raychem Corporation Austenitic aging of metallic compositions
US4019925A (en) * 1974-05-04 1977-04-26 Osaka University Metal articles having a property of repeatedly reversible shape memory effect and a process for preparing the same
DE2516749A1 (de) * 1974-05-04 1975-11-20 Univ Osaka Metallkoerper mit reversiblem gestaltwechselvermoegen und verfahren zu deren herstellung
US4055445A (en) * 1974-09-20 1977-10-25 Essex International, Inc. Method for fabrication of brass alloy
US4099991A (en) * 1974-10-10 1978-07-11 Essex Group Method for effecting reverse shape memory phenomena in Cu-Zn-Si brass alloy
US4036669A (en) * 1975-02-18 1977-07-19 Raychem Corporation Mechanical preconditioning method
DK156254B (da) * 1975-02-18 1989-07-17 Raychem Corp Fremgangsmaade til fremstilling af en varme-restituerbar genstand af et metalmateriale, der kan undergaa reversibel omdannelse mellem en austenitisk og en martensitisk tilstand
US4296955A (en) * 1975-04-09 1981-10-27 Raychem Corporation Composite coupling device with high recovery driver
US4144104A (en) * 1976-03-18 1979-03-13 Raychem Corporation Stable heat shrinkable ternary β-brass alloys containing aluminum
US4146392A (en) * 1976-03-18 1979-03-27 Raychem Corporation Stable heat shrinkable ternary beta-brass type alloys containing manganese
US4166739A (en) * 1976-03-18 1979-09-04 Raychem Corporation Quarternary β-brass type alloys capable of being rendered heat recoverable
US4113475A (en) * 1976-04-09 1978-09-12 Kennecott Copper Corporation Tarnish resistant copper alloy
US4285739A (en) * 1977-12-28 1981-08-25 Leuven Research And Development Vzw Process of manufacturing solid bodies of copper-zinc-aluminium alloys
DE2900518A1 (de) * 1978-01-09 1979-07-19 Raychem Sa Nv Verfahren zur bildung einer dichten abzweigenden verbindung und zur durchfuehrung des verfahrens bestimmte klammer
DE2954743C2 (de) * 1978-01-09 1996-10-31 Raychem Sa Nv Verfahren zur Bildung einer dichten Verbindung zwischen einer wärmegeschrumpften Muffe und wenigstens zwei langgestreckten, vom gleichen Ende in die Muffe eintretenden Substraten
US4274872A (en) * 1978-08-10 1981-06-23 Bbc Brown, Boveri & Company Brazable shape memory alloys
JPS56136945A (en) * 1980-03-03 1981-10-26 Bbc Brown Boveri & Cie Shaped memory alloy based on cu al or cu al ni and stabilization of said alloy in two-direction effect
EP0035070A1 (de) * 1980-03-03 1981-09-09 BBC Aktiengesellschaft Brown, Boveri & Cie. Gedächtnislegierung auf der Basis eines kupferreichen oder nickelreichen Mischkristalls
EP0035602A1 (de) * 1980-03-03 1981-09-16 BBC Aktiengesellschaft Brown, Boveri & Cie. Verfahren zur pulvermetallurgischen Herstellung einer Gedächtnislegierung auf der Basis von Kupfer, Zink und Aluminium
WO1981002587A1 (en) * 1980-03-03 1981-09-17 Bbc Brown Boveri & Cie Memory allows with a copper,zinc and aluminum base and method for preparing them
US4365996A (en) * 1980-03-03 1982-12-28 Bbc Brown, Boveri & Company Limited Method of producing a memory alloy
US4389250A (en) * 1980-03-03 1983-06-21 Bbc Brown, Boveri & Company Limited Memory alloys based on copper or nickel solid solution alloys having oxide inclusions
JPH0138867B2 (xx) * 1980-03-03 1989-08-16 Asea Buraun Boeri Ag
EP0035601A1 (de) * 1980-03-03 1981-09-16 BBC Aktiengesellschaft Brown, Boveri & Cie. Verfahren zur Herstellung einer Gedächtnislegierung
US4781606A (en) * 1980-12-12 1988-11-01 Raychem Corporation Wire stripping arrangement
JPS57175640A (en) * 1981-04-21 1982-10-28 Matsushita Electric Ind Co Ltd Roller unit
US4621844A (en) * 1982-01-25 1986-11-11 Shell Oil Company Memory metal connector
US4448824A (en) * 1982-01-28 1984-05-15 Raychem Corporation Wraparound protective closure
US5088772A (en) * 1984-11-14 1992-02-18 N. V. Raychem S.A. Joining insulated elongate conduit members
US5002716A (en) * 1984-11-14 1991-03-26 Raychem Corporation Joining insulated elongate conduit members
US4872713A (en) * 1987-02-19 1989-10-10 Raychem Corporation Coupling device
US4832382A (en) * 1987-02-19 1989-05-23 Raychem Corporation Coupling device
US5362141A (en) * 1990-04-27 1994-11-08 Alfred Teves Gmbh Valve block and method of assembling an element thereto
WO2003035918A2 (en) * 2001-10-22 2003-05-01 Council Of Scientific And Industrial Research Cu-zn-al(6%) shape memory alloy with low martensitic temperature and its process
WO2003035918A3 (en) * 2001-10-22 2003-11-13 Council Scient Ind Res Cu-zn-al(6%) shape memory alloy with low martensitic temperature and its process
US20090065103A1 (en) * 2007-09-10 2009-03-12 Sippola Pertti J Method and apparatus for improved formability of galvanized steel having high tensile strength
WO2009035576A1 (en) * 2007-09-10 2009-03-19 Sippola Pertti J Method and apparatus for improved formability of galvanized steel having high tensile strength
US10160063B2 (en) * 2014-11-18 2018-12-25 Baker Hughes Incorporated Braze materials and earth-boring tools comprising braze materials
US10807201B2 (en) 2014-11-18 2020-10-20 Baker Hughes Holdings Llc Braze materials and earth-boring tools comprising braze materials
CN105063427A (zh) * 2015-08-28 2015-11-18 中国科学院金属研究所 一种磁兼容锌合金及其应用

Also Published As

Publication number Publication date
NL7016616A (xx) 1971-05-14
CH580167A5 (xx) 1976-09-30
SE389690B (sv) 1976-11-15
NL172766C (nl) 1983-10-17
IL35632A (en) 1974-09-10
IL35632A0 (en) 1971-01-28
BR7023837D0 (pt) 1973-02-27
CA970670A (en) 1975-07-08
BE758862A (fr) 1971-04-16
JPS5511740B1 (xx) 1980-03-27
FR2067253A1 (xx) 1971-08-20
USRE31474E (en) 1983-12-27
DE2055755A1 (de) 1971-05-19
NL172766B (nl) 1983-05-16
FR2067253B1 (xx) 1973-02-02
DE2055755C2 (de) 1986-12-04

Similar Documents

Publication Publication Date Title
US3783037A (en) Treatment of alloys
US4631094A (en) Method of processing a nickel/titanium-based shape memory alloy and article produced therefrom
US4707196A (en) Ti-Ni alloy articles having a property of reversible shape memory and a method of making the same
JPH0411617B2 (xx)
US4533411A (en) Method of processing nickel-titanium-base shape-memory alloys and structure
US4654092A (en) Nickel-titanium-base shape-memory alloy composite structure
US4067752A (en) Austenitic aging of metallic compositions
US3802930A (en) Alloys
JPH0251976B2 (xx)
US6010584A (en) High temperature shape memory effect in ruthenium alloys
EP0187452A1 (en) A method of processing a nickel/titanium-based shape memory alloy and article produced therefrom
Duerig et al. Wide hysteresis NiTiNb alloys
JPS6361377B2 (xx)
JPS61119639A (ja) ニツケル／チタン／ニオブ形状記憶合金および物品
JPS6247937B2 (xx)
Brook Gold alloys with shape-memory
Nakanishi Lattice softening and the origin of SME
JPS6144150B2 (xx)
US3989552A (en) Method of making a heat-recoverable article
JPS624462B2 (xx)
Dutkiewicz et al. Stabilisation of Martensite in Cu-Zn-Si
KR820001567B1 (ko) 금속조성물의 오스테나이트에이징 방법
JP4017892B2 (ja) 高い振動減衰性能を有する合金の製造法
US3989551A (en) Method of making a heat-recoverable article
JPH0128252B2 (xx)