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`SOVIET PHYSICS
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`8)August 19792—
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` a translation of the ”Physics Sections” of AOKHAAH AKA EMHH HAYK CCCP’ Doklady Akademii
`
`——v
`
`Nauk SSSH (Proceedings of the Academy of Sciences of the SSH), V01. 24?, Nos. 4-6, Aug. 1979
`
`published by the American lnstitu
`
`of Physics
`
`Edwards Exhibit 1023, p. 1
`
`Edwards Exhibit 1023, p. 1
`
`

`

`ISSN: nose-sea”;
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`Soviet Physics—Dckiao'y. a translation of JIOHJIAJIBI AHMEMHH
`HAVE CCCP, DoiriadyAiradenrii Nadir SSSH. is a monthly Journal published
`by the American Institute of Physics lor the purpose of making available In
`English reports of current Soviet research in physics as contained in the physics
`sections of the Proceedings of the Academy oi Sciences of the USSR. The
`Proceedings appear 36 times per year. and the physics sections are accumulat-
`ed and English translations of them are published in 12 issues per year. The
`translations began with the 1956 issue.
`
`SovietPhysics—Dok/ady is translated and produced for the American Institute
`of Physics by Consultants Bureau. a division of Plenum Publishing Corporation.
`One volume is published annually.
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`The American Institute of Physics and its translators propose to translate faith-
`fully all the material appearing in the original articles. The views expressed in
`the translations are therefore those of the original authors. and not of the trans-
`lators nor of the American Institute of Physics. The transliteration of the names
`of Russian authors follows essentially the standard agreed upon by the British
`Standards institute and the American National Standards Institute.
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`Copyright 1980. American Institute of Physics. Individual readers of this laur-
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`Edwards Exhibit 1023, p. 2
`
`

`

`The multiplicity of structural transitions in alloys based on TiNi
`
`I. Peskal'. V. E. Gyunier, L. A. Monasevich. and E. M. Sevilskil‘
`D. B. Chernov, Yu.
`A. A. Balkan Institute cherallurgy. Academy of Sciences of the USSR. Moscow
`(Submitted March 29, 1979)
`Bold. Mind. Nauk SSSR 247. 854-357 (August
`
`l9'l9)
`
`PACS numbers: 64.70.Kb, 61.50.Ks. 61.55.Hg
`
`This material may be protected by Copyright law (Title 17 US. Code)
`
`1
`
`The structural transformations in alloys based on TiNi
`have been the object of intensive research. since these
`alloys exhibit a "memory" effect and are used in various
`areas of technology. However. an accurate picture of the
`structural transitions has not yet been obtained and the
`literature on the subject shows considerable disagree-
`ment.“ Including. in some cases. the publication of mus
`tually exclusive resultedv" In our opinion these dls~
`agreements are caused by the fact that in the interprets-
`tlon of the experimental data the multiplicity of structural
`transformations in the alloys investigated was not taken
`into account. The present work is deVoted to the deter-
`mination of the character and the order of the structural
`transitions in Ti-Nl alloys as a function of composition
`and temperature.
`
`Our preliminary world5 showed that the high-temper-
`ature phase. with the B2 structure (CsCl bcc structure).
`may. depending upon the composition. transform directly
`to a 1319' structure (rhomblc 1319 structure with additional
`monoclinlc distortion) or may instead transform to a. thorn-
`bohedrai phase B which. upon further cooling. transforms
`in turn to the 1319' phase.
`
`The work described here was carried out on binary
`Ti—Ni alloys and ternary Ti—Ni—tli‘e alloys with an equi-
`atomic relationship Ti/ (Ni + Fe). The alloys were smelted
`from titanium iodide and electrolytic nickel and subjected
`to multiple electric-arc melting. After forging. the cast—
`ings were rolled into a strip of thickness 1.5 mm for x-
`ray diffraction studies or were drawn into a wire of diam—
`eter 1 mm for
`electrical-resistance measurements.
`The studies were carried out after annealing for one hour
`at 800°C without preliminary cycling in the range of the
`transformations.
`
`It was observed that the monoclinlc Bls‘ phase formed
`directly from the 132 underwent triciinic distortion upon
`further cooling and transformed to a. 1319" structure. as
`
`
`
`mm
`C
`A
`
`
`_ "7i? _'-__—W 50 RM
`
`
`
`D
`
`1W. iii.
`
`Typical curves of the temperature dependence of the
`(110}32 peak intensity and the ratio c/a. correspondl-ns
`to different regions of the transformation diagrams (Filli-
`1 and 2). are shown in Fig. 3. The rhombohedral distof'
`tion c/a was determined for hexagonal close-packing-
`‘I‘he cubic system corresponds to c/ a = 1.224.
`
`
`
`indicated by the regular broadening. i.e.. the unresolvahl'n.
`splitting of certain powderhpattorn lines associated With
`the inotiociinlo structure as the temperature was lowered,
`The transformations 1319' $3319". like B2 an. cannot
`be distinguished experimentally from second—order trans
`sitions, while the transformations B2 #B19' and R gamut
`are typical firstmorder marteneitic transformations.
`in '
`contrast. the 3319' phase formed from It does not experi-
`ence any transformations upon cooling to—~156°C. As—
`suming that the 1319' phases formed from B2 and from R
`are somewhat different in their parameter values. we may.
`expect that both phases will coexist in some concentra-
`tion interval. However. verification of these conjecture!
`is difficult. since the difference between the phases is at
`the limit of sensitivity of the techniques employed.
`
`‘
`
`The extent of the martensltic transformations 32 en
`1319' and R #BlB' was estimated in two ways from the it-
`ray diffraction data: as the ratio of the pealc intensity
`l
`of the (101)3191 line to its maximum value below My. and
`as the ratio of the intensity of the (110m; line to Its mule" '
`mum value in the absence of the martensitic phases. The
`two methods gave consistent results except when the tem-
`perature interval of the single-phase state R upon cooling
`was very wide. The temperature TR of the transition
`B2 :15! was determined from the onset of the broadening
`of the upper part of the intensity profile of the (11mm
`line: this broadening precedes the rhombohedral splitttnfl.
`of this line. The temperature T'I'r of the transition B19' e-
`B19Ill was determined from the onset of the regular broad--
`enlng of the (lullei line.
`
`.
`
`*
`
`
`
`Edwards Exhibit 1023, p. 3
`
`

`

`
`
`.m an an
`
`a:
`
`
`
`l
`
`#20 '5
`“2W - 12‘0
`-tll
`W
`
`n6. 3, Typical temperature dependence: of the peak intensity or the
`mo“, line (solid curves) and the degree of rhomhohedrai distortion c-‘n
`(“mid curve!) in the range of the transformutlon in various regions of
`mg mnsformntion diagrams off-'13:. i and e.
`
`The ellctricfll resistance was measured by the emu
`meterevoltrneter method with careful stabilization of the
`clarinet and direct recording on an xy automatic record-
`int; instrument. The martensitlo points of the B2 #1319
`and R afllQ' transitions were determined in the usual
`ill-BU as parameters ol‘the hysteresis loop, while the tem-
`perature TR of the BE -.—-ell transition was determined as
`the temperature of the onset of the resistance increase
`“compile-lying the rhombohedral distortion of the cubic
`phase. Typical curves of the variation of the electrical
`resistivity upon cooling and heating in the range of the
`mlormatlons are shown in Fig. 4.
`
`The transformation diagrams for the binary system
`are shown in Fig. 1. For concentrations of nicltel below
`50% of the martonsitic points are practically independent
`iii composition, owing to the unavoidable two-phase characm
`tor of the original material (Ni'l‘i + Ni’l‘igl and conse-
`quently of the constant (equilibrium) composition of the
`high-temperature phase (132) of NiTi. The line T3 In Fig.
`[intersects the line M3 at 50.3% Ni. the line As at 503%
`'NL and the line Af near 51% Ni. For nickel contents her-
`law 46.75% the point TR falls below Mf and the BE =R
`Mitten is not realized. As pointed out above. in alloys
`oi this composition the B19' #319" transition occurs (at
`“EO'CJ. We note that cycling in the temperature interval
`0.1 the transformations lowers the polntsMs. Mf . As. and
`A)! to a larger degree than the point TR- with the result
`that the points of intersection of the TR line with the cor-
`“Spending curves are displaced to the left.
`
`Introduction of iron into the alloy in place of nickel
`‘
`llamas a large lowering of the points M3. Mf. As. fmd Af
`“130001 Elgreemenl‘. with data obtained earlier on alloying
`“We a section of the 'l'iNi-Fe diagramfi The lowering of
`the point TB is less pronounced. with the result that the
`region of the complete transition BB ==R appears for iron
`concentrations greater than 1.25%.
`
`In the various regions ol‘ the diagrams in Figs. 3 and 4.
`It
`9 following sequences of direct transformations are‘
`
`FIG, 4, Typical curve! of the temperature dependence of the electrical
`resistance In the range of the transformations in various regions of the
`transformation diflgrflms of Figs. 1 and '2.
`
`observed:
`
`to as: +Bl9' esw' +319" (in region A).
`32 +132 +sia' +R +slc’ 4 319' {in region is),
`in 4:12 +12 +319' acid (in regions (3, c. and E);
`while the reverse transformations are:
`
`319"+319’ 4319' +32-BZ rlnrcgmn A).
`319' an +R +32 +32 (in regions is and C),
`319' 4319' +11 ems' +32 4.82 (in region DJ,
`1119' +319’ +a 4R M): (in region a).
`
`in the transformation diagrams. regions with different
`positions of the line TR with respect to the lines denoting
`the beginning and end of the marteusitic transformations
`are distinguished: Afr“ < Mf); B(Mf < TR < MB);
`C(Ms < TR 6. AH); DmE < TR «1 Af); and EiTR p Af).
`In the region E the only tanSition obserVed above -—196°C
`in B2 =R.
`
`The multiplicity of ditfusionless structural phase tran-
`sitions in alloys with a specific chemical composition is
`a typical and, apparently, general characteristic of such
`transitions. This multiplicity of transitions and their
`products is not a manifestation of Ostwald's rule of stages.
`since the phases transform into each other not by a time-
`dependent process with constant external conditions. but
`rather by change of these conditions. The specifics of
`each diffusionless process, exhibiting all or some of the
`classical indications of martensitic ltll‘ieties.7 are Such
`that the final state for a given set of external conditions
`is reached very rapidly and, in the absence of diffusion
`processes, will last for an indefinitely long period if the
`external conditions are held unchanged. Hence. the prod-
`ucts of the various transitions are related not as meta—-
`
`stable and stable phases. but as phases that are candid
`tlonally stable in the presence of additional limitations on
`the diffusion and relaxation processes. These phases are.
`of course, metastable with respect to the State that would
`be attained in the presence of diffusion processes.
`The transformation diagrams constructed may serve
`as a. guide In the selection of the composition of materials
`
`Sov. Phys. Dokl. 24lfll, Annual 1979
`
`Chelnov at al.
`
`l.“
`l
`
`Edwards Exhibit 1023, p. 4
`
`Edwards Exhibit 1023, p. 4
`
`

`

`'
`
`exhibiting a shape—memory effect, since all the memory
`effects - in particular. the thermomechanical character~
`istlcss'B and the reversible shape-change effect.1° depend
`on the specific sequence of transformations. For exam-
`ple. in the region A there is a clear separation between
`the temperature regions of the B2 t.——-R and R :BIQ' trans—
`formations. with the conseqaenoe that a two-stage shape-
`memory etfect is observed here.
`
`'Corrslpnnding member. Academy of Sciences of the USSR.
`
`'6. R. Partly and l. c. m. Tram. AIME as}, set r1931).
`’1’. E. Wang. W. l. Buchler. and s. I. Pickett. J. App}. new, gig, 32:32
`(1985).
`
`3J. E. Hnnlon. S. R.
`(1961').
`
`liutlcr. and R. I, Wnailewnkl. Tram. “MILE-E. 1323
`
`‘I. l. Kornllov. E. V. Kachur. and O. K. Belnuaov. Fin. Met. Metallovgd
`'
`rfl' No. 2. 42:; can).
`v. N. Kliachin. V. ll. Gyunter. et a!" Dotti. Akad. Nauk SSSR £31, 1059
`(1917) (Sou. Phys. Dasha. 336 (1977)].
`EE). 8. Chemov. 0. K. Beluusov. and D. A. Murrow, Metallowd. Tam“
`Obi-ah. Met“ No. 2. '72 (1978).
`To. v. Kurdyumov. 1h. The. Fla. is No. a, 999 (1948).
`''N. F. thbyneva. and D. B. Chetnov. Methiloved. Term. Ola-ab, Men.
`No. 10. 10 (1975).
`_
`at). it. Chernov. L. l'. Fatitullna. cl: 3]..
`'I'ekhnol. Legitilth Splnvw, Na. 5'
`as (last).
`,
`I"tr. N. lChtchln. V. E. Gyuntcr. and D. B. Chemov, Fla. Mat. Moreno”
`E, No. a. car; (1976).
`
`Translated by K. B. Lyons
`
`Features of the heating of matter by specially profiled radiation
`
`V. K. Ablekov. Academician V. S. Avduevskii. Yu. N. Babeev.‘ and A. M. Frolov
`(Submitted April 4,
`l979)
`Dokl. Akad. Neck SSSR 247.
`
`|l37~ll40 (August 1979)
`
`PACS numbers: 52.50.Gj. 72.30. + CI
`
`The problem of the heating of matter by radiation is
`basically determined by the physics of the introduction of
`electromagnetic energy and by the mechanisms of transfer
`of energy from the electrons to the ions of the plasma of
`the substance.
`
`In the present work we consider the mechanism of the
`heating of the ions of a dense plasma and of a metal lat-
`tice. and its dependence on the energy of the intense in-
`cident radiation.
`
`We consider a metal in the I'cold-plasma'l model —
`i.e.. we do not consider kinetic effects in the electron gas.
`The electron gas is assumed to be degenerate up to a
`temperature To (To is the degeneracy temperature). Hence
`we may restrict our attention, below this temperature. to
`electrons located near the Fermi level. The dispersion
`properties of the plasma and metal are not taken into ac-
`count. We consider the spatially uniform formulation of
`the problem.
`
`the heating of the electron gas. we can assume that the
`heating of the electrons and the metal lattice is described
`by the equations
`'
`
`c.% = [E- 6'»... (T. — n).
`31"
`c. —' =5'.:.. (1". — n),
`ar
`
`5.». =5'.
`
`it!
`-
`(‘1
`
`where 6 is the elastic-collision emfflcient of the else-
`trons with the metal lattice or with the ions of the plasma.
`For metals1
`
`I m. c’I u
`5: "—
`6
`0.?“
`
`hi.
`
`where as is the speed of sound. while [or a plasmall
`
`The electrons in the plasma or metal move in the
`field of a transverse wave at the form
`
`E-Eo sin wt.
`
`(1)
`
`Assuming that d is a. constant. i.e., is independent 01'
`the relative velocity of the electrons and ions, we ohm”
`a solution of the system (1)44} in the form
`
`
`
`The motion of an electron in the light-wave field obeys
`the equation
`
`Bu.
`ch},
`a!
`mu
`
`sin to! — v. .14..
`
`'(2)
`
`where “61 is collision frequency of electrons with the ions
`or with the metal lattice.
`In the general case. the colli-
`sion frequency depends on the direction of the electron
`velocity.
`
`Assuming that the time of action is small compared
`
`T. — Ti '-u sin“ wr vb sin to: cor wt.
`
`T. shy“ (F H. 4+ it sinI on);
`3
`to
`
`e‘nhé
`-.
`,_
`u t-c =
`‘
`6 (.2 + as.)
`
`where
`
`y
`g, =51 _‘._l
`
`-
`
`
`ENE:
`—
`o
`
`x
`
`in
`
`idi-
`..
`m
`
`
`
`Edwards Exhibit 1023, p. 5
`
`