US3174851A - Nickel-base alloys - Google Patents

Nickel-base alloys Download PDF

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Publication number
US3174851A
US3174851A US157049A US15704961A US3174851A US 3174851 A US3174851 A US 3174851A US 157049 A US157049 A US 157049A US 15704961 A US15704961 A US 15704961A US 3174851 A US3174851 A US 3174851A
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US
United States
Prior art keywords
tini
alloys
percent
alloy
temperature
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Expired - Lifetime
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US157049A
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English (en)
Inventor
William J Buehler
Raymond C Wiley
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Individual
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Priority to US157049A priority Critical patent/US3174851A/en
Priority to DK513762AA priority patent/DK105237C/da
Priority to AT940562A priority patent/AT247623B/de
Priority to GB45517/62A priority patent/GB1020872A/en
Priority to CH1407862A priority patent/CH433772A/de
Priority to NL62286263A priority patent/NL143279B/xx
Application granted granted Critical
Publication of US3174851A publication Critical patent/US3174851A/en
Priority to NL7410044A priority patent/NL7410044A/xx
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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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
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
    • F03G—SPRING, WEIGHT, INERTIA OR LIKE MOTORS; MECHANICAL-POWER PRODUCING DEVICES OR MECHANISMS, NOT OTHERWISE PROVIDED FOR OR USING ENERGY SOURCES NOT OTHERWISE PROVIDED FOR
    • F03G7/00—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for
    • F03G7/06—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like
    • F03G7/065—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like using a shape memory element
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01K—MEASURING TEMPERATURE; MEASURING QUANTITY OF HEAT; THERMALLY-SENSITIVE ELEMENTS NOT OTHERWISE PROVIDED FOR
    • G01K5/00—Measuring temperature based on the expansion or contraction of a material
    • G01K5/48—Measuring temperature based on the expansion or contraction of a material the material being a solid
    • G01K5/483—Measuring temperature based on the expansion or contraction of a material the material being a solid using materials with a configuration memory, e.g. Ni-Ti alloys

Definitions

  • This invention relates to a series of novel structural alloys of the intermetallic compound type which are characterized by unusual mechanical and physical properties.
  • intermetallic compounds other than TiNi, are very brittle, lack any form of ductility at room temperature and in spite of many other outstandingly good properties displayed by these compounds, such as strength maintenance at high temperatures, their brittleness at room temperature has made these compounds virtually useless in structural applications except as minor strengthening constituents in a more ductile matrix metal or alloy.
  • Novel intermetallic compound base materials of the TiNi type have now been discovered which not only possess the desirable properties characteristic of intermetallic compounds in general but also possess hitherto unknown and unusual properties.
  • intermetallic compounds as a general term is considered hereinafter as an intermediate phase in an alloy system, having a reasonable range of homogeneity and relatively simple stoichiometric proportions, in which the nature of the atomic binding can vary from metallic to ionic, and further includes all intermediate phases in binary and higher order metal systems whether ordered or disordered.
  • These intermetallic compounds are combinations of two or more metals, the atoms of such metals generally being in a simple whole number ratio. In the majority of cases, however, the formulas of intermetallic compounds do not agree with formulas based on the principle of valency.
  • TiNi Ti Ni+TiNi They were prepared as illustrated in the following detailed example.
  • EXAMPLE The raw materials used were Mond nickel shot and commercially pure titanium bar stock.
  • the preparation of the novel intermetallic TiNi alloys may be divided into three distinct steps as follows:
  • All of the cast alloys between about 52 to 56 weight percent nickel and correspondingly between about 48 to 44 Weight percent titanium may be hot worked without any preliminary heat treatment.
  • a stoichiometric TiNi composition of 55.1 weight percent nickel and 44.9 weight percent titanium was readily hot worked in the as cast condition between about 650 C. to about 1100 C., the preferred hot working temperature range being from about 700 C. to 900 C.
  • Alloys containing above 56 weight percent nickel, that is from about 56 to 64 weight percent nickel required a preliminary heat treatment to render them hot workable. This heat treatment consisted of heating the alloys to about 1050 C. until heated through and then slowly cooling to room temperature. Alternatively, the alloys may be heated to about 1050 C. until heated through, cooled slowly to about 850 C. and held at that temperature until heated through and subsequently allowed to slowly cool to room temperature.
  • the principle behind the above pre-working heat treatments is to precipitate and coalesce the excess compound phase TiNi3 from solution with the compound phase of TiNi. This results in a ductile TiNi matrix interspersed with the more brittle TiNi compound coalesced into harmless particles. Following the above described alternative pre-working heat treatments the two phase TiNi-l-excess TiNi alloy was capable of being rolled at any temperature between about 700 C. to about 900 C.
  • alloys containing between about 56 to 64 weight percent nickel are very much affected by heat treatment and particularly by the cooling rate. These alloys when heated to above about 900 C. and quenched in room temperature water .attain a high hardness. For instance, an alloy of about 60 weight percent nickel and about 40 weight percent titanium yielded, when quenched from between 900 C. and 1110 C., a hardness varying between 58 R and 62 R as may be seen from Table I.
  • the hardness of quench-hardened alloy (56 to 64 wt. percent Ni, remainder Ti) components may be reduced to a lesser degree of hardness if such is required for a specific application. Such reduction must be based upon the best compromise of mechanical properties for the particular application. Reduction of hardness of quenchhardened all-oys may be accomplished by (A) slowing down the cooling rate of the heat treated component to yield hardnesses between about 35 R (furnace cool) and about 62 R (water quench) and by (B) tempering.
  • This tempering process is accomplished by reheating the quench-hardened alloy to various temperatures below the point of change in slope of the phase boundary between the TiNi and TiNi-i-TiNi phase areas (about 900 C.) and cooling at a specified slow rate, the final tempered hardness being determined by the heating temperature, period of time at the heating temperature and the rate of cooling.
  • the above hardening and tempering heat treatments may be performed in a controlled atmosphere of helium or argon. In many applications, however, heat treatment in air will sufiice.
  • the room temperature hardness increases with an increase in rolling temperature which is undoubtedly related to the higher temperature of heatingand fairly rapid cooling rate from temperature. It may also be seen that while the Ti Ni composition alloy is quite hard (53 R the TiNi compound has a hardness (34 R more like that of the TiNi alloy. Yet in spite of the much lower hardnessexhibited by TiNi it is similar to the Ti Ni compound in that it is brittle even at high homologous temperatures.
  • test sections were finish lapped in the longitudinal direction to avoid any possible transverse notches.
  • vacuum or controlled atmosphere heat treating was used. Vacuum heat'treating was performed in an evacuated quartz tube. The tensile test results obtained from the two TiNi alloys are shown in Table IV.
  • a paramagnetic material has been defined as a material whose specific permeability is greater than unity and is practically independent of the magnetizing force.
  • the nickel-titanium alloys in the composition range which covers Ti Ni, TiNi, and TiNi are highly paramagnetic, in spite of the high amount of nickel present in there alloys.
  • Alloys of the 54 to 60 w/o Ni, remainder Ti composition have been magnetically evaluated after various thermal treatments and at widely varying temperature. The magnetic testing included both magnetic susceptibility and permeability measurements. In these tests it was found that the permeability approached extremely close to unity regardless of the temperature, residual stresses, or prior thermal treatment. Care must be exercised to remove any oxide coating in cases where the TiNi-base alloys are to be used in non-magnetic applications. This is caused by the combination of some Ni of the base alloy with O to form a ferromagnetic oxide coating.
  • the phase equilibria theory is further confirmed by the fact that alloys containing excess Ni or excess Ti over the stoichiometric composition have distinctly different room temperature damping properties.
  • the Tib cs rich alloys (less than 54.5 w/o Ni) are highly damping at room temperature, while alloys on the Ni-rich side (in excess of 54.5 w/o Ni) show low damping at room temperature, thus indicating that the Ti Ni phase coupled with the liNi produces the high damping capacity.
  • Anything lessening the Ti Ni phase e.g. increased Ni, higher temperatures, impurity atoms like Fe, etc. causes minor changes in the TiNi/Ti Ni phase equilibria and thus promotes drastic vibrational damping changes- This unusual damping phenomenon may lead to the utilization of these alloys as temperature sensing devices.
  • novel TiNi alloys containing from about 50-70 wt. percent Ni have been discovered which possess the unusual combination of properties of high hardness at wide temperature variations and especially at temperatures Well below freezing and having unusually good ductility. and impact strength at these same temperatures.
  • the alloys may be subdivided into those alloys having a range of about 52 to about 56 wt. percent Ni (remainder Ti) and those alloys containing from about 56 to about 64 wt. percent Ni (remainder Ti).
  • the former are characterized by the existence of an almost wholly TiNi phase, by being readily workable whether hot or at room temperature and by exhibition of unusually high ductility at room temperature.
  • the latter alloys are characterized by being two-phase materials (TiNi-I-TiNig) capable of being hardened to'high hardness levels.
  • Magnetic susceptibility (mass, -196 to 550 C.) 5-9 10' [Mechanical] 54.5 w/o Ni V 55.1 w/o Ni Ultimate Tensile Stn, p.s.i-..- 110,000-124,000- 82,000-140,000.
  • a novel alloy composition consisting essentially of from about 50 percent to about 70 percent nickel by weight and correspondingly from about 50 percent to about 30 percent titanium by weight, said alloy having the structure of a TiNi phase in combination with a TiNi pha-se dispersed in a TiNi matrix within a temperature range of from about 500 C. to about -75 C. and having the properties of being paramagnetic, of retaining hardness throughout said temperature range and of being corrosion resistant.
  • a novel alloy composition consisting essentially of from 52 percent to about 5 6 percent nickel by weight and correspondingly from about 48 percent to about 44 percent titanium by weight, said alloy having the structure of a substantially TiNi phase within a temperature range of from about 500 C. to about 75 C. and having the properties of being paramagnetic, of being highly vibration damping at about room temperature and having the capability of being plastically deformed at about room 1t) temperature and retaining the deformed shape until heated to a higher temperature whereupon the prior nondeformed condition will be reassumed.
  • a novel alloy composition consisting essentially of from about 56 percent to about 64 percent nickel by weight and correspondingly from about 44 percent to about 36 percent titanium by weight, said alloy having the structure of a substantially TiNi phase dispersed in a TiNi matrix within a temperature range of from about 450 C. to about 75 C. and having the properties of being paramagnetic, of high hardness upon heat treatment, of being abrasion and corrosion resistant and capable of being hot wrought into useable shapes prior to hardening.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Combustion & Propulsion (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • General Engineering & Computer Science (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • General Physics & Mathematics (AREA)
  • Heat Treatment Of Steel (AREA)
  • Manufacture And Refinement Of Metals (AREA)
US157049A 1961-12-01 1961-12-01 Nickel-base alloys Expired - Lifetime US3174851A (en)

Priority Applications (7)

Application Number Priority Date Filing Date Title
US157049A US3174851A (en) 1961-12-01 1961-12-01 Nickel-base alloys
DK513762AA DK105237C (da) 1961-12-01 1962-11-29 Let smeltelig, bearbejdelig og korrosionsbestandig nikkellegering.
AT940562A AT247623B (de) 1961-12-01 1962-11-30 Legierung
GB45517/62A GB1020872A (en) 1961-12-01 1962-11-30 Nickel-base alloys
CH1407862A CH433772A (de) 1961-12-01 1962-11-30 Nickellegierung
NL62286263A NL143279B (nl) 1961-12-01 1962-12-03 Werkwijze voor het vervaardigen van voorwerpen van een nikkeltitaanlegering alsmede op deze wijze vervaardigde voorwerpen.
NL7410044A NL7410044A (da) 1961-12-01 1974-07-25

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US157049A US3174851A (en) 1961-12-01 1961-12-01 Nickel-base alloys

Publications (1)

Publication Number Publication Date
US3174851A true US3174851A (en) 1965-03-23

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Family Applications (1)

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US157049A Expired - Lifetime US3174851A (en) 1961-12-01 1961-12-01 Nickel-base alloys

Country Status (6)

Country Link
US (1) US3174851A (da)
AT (1) AT247623B (da)
CH (1) CH433772A (da)
DK (1) DK105237C (da)
GB (1) GB1020872A (da)
NL (2) NL143279B (da)

Cited By (375)

* Cited by examiner, † Cited by third party
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AT247623B (de) 1966-06-27
DK105237C (da) 1966-09-05
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NL7410044A (da) 1974-10-25
CH433772A (de) 1967-04-15

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