SCIENTIFIC ABSTRACT SAVITSKIY, YE.M. - SAVITSKIY, YE.M.

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• Collection: Scientific Abstracts
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• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT


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CK THS URDru CF 141CRGTu1SM 5FB%;I!-iaW5. aLiavitakii. w-AVP
Lebedev. Layodle yaa '~aborator iya 1949, Vol- I pp. 614.416
In Russian. Techniques suita ble for the te-iting of sreciments
of di&zetevs or the order of ~ 1 = are described. In these
methods the specimens'are hold in a manner which facilitatels
testing at high t emperature3.
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S.S~S.M. 67. Nl_.1tl9p)V: 1, CA- 43, 217174- ContrAry
so la expeo-tatwor, the bjntno~,.4 %lr~Al alkyv~ to the ea"e
00 41 MK. where the %tate dwgrmn -4- A oc
plu,^ or thrir mixt.. k additive on1v At low truil-, bur
00 or low (nnn 300" upvoirds. At 30). 1141..41111 4:14)'. tile Al-
oe ImN are misch move plastic thAtt rithvr the it or the )
ltsioe: thu,,. at 4.'4)'. the luninoi to[ the:LS.9r; Nix alloy
,
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ch.ing" on hearing in 4(1()' ill the e4v of allfryi rlionmmic
so ap 'ooly of either the 0 or tile -t phaic. lf,l%rvrr, "ouplo,,
00 --hich. in lbrannratrif mair, at W', J)"well to lWa 11%11(-
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Lg.Sjr, %I,.
of file A Anil the'l, I,ILLW, ,,
."11V fill- if .1 'ingle ph.1'e, 'Jiffsfriol fr,,Ivl 1%,th ;I allot 'p.
00
cl-orr P- the lattorr trot witha ~inoplev, lAttice. ~ Mori, voish
Mg, bellell to, IfW and quenched ill i-
water. %howecl, in nkimrcraphy. stnicturr. in
"ontrast to the tuo-plLoe stettertiro: of the Anticall:41 Aloy-
The x-ray lialftaill of fluenched imple, taken :it
Aly of the bilth-tenilo, hiriln"% rurvi, a% a futictimi of Me
ritntlon., in Mx ranxv. k -file to th, inxt-
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VN"ductism of Delsirroled T*l4 Sperimsesm F~rmso hWer-
nwildhe Compounds. (In Russian-) F '00
_it,_ 4UL V.
V. Baron. and M. A. Tylkina. 7A-r; koya
I-riya (Factory 1,&~orxtory). v. 15, June lii4D, p. -00
729-732.
Develops methotl an,l apparalus for ppuluctiool it .00
the above by h,,t presArne and hot extru.-ion.
800
Sh,,wx that the conct-lit of intermetallic compoin,14
a4 brittle substnncto i- corn,-t only liver a tictinite =00
temptrature ranire, and that such ciont-un.1- lm-
*0 have as pInAtie %uhstance* uncler certain conififi-mat. ZOO
*0 a Defornliki t"t xf~vcimrto (it the intertnetallic
(,~Mppund.- of Mirzis, and 31ell~ and .,f
roe
the intormetallir $0 and *t Pha.%- in the AJ-Slj~
system with different, concentrationt, (if cornimm-
ents wvr,- obtained. 2 jr* 0
.as,
ASA~SLA OEIALLUOCK41 WFOLIWIff CLASSIFIC&Mv
I!= "~AA I
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a
S.S.S.R. 73. 945-709W)~-A literature survey showed
that 16 of 19 polymorphic metals had a cu. lattice for their
himbeg-temp. form, and, therefore, these metals had high
pj"tWty at hilgh tsmPa. L It sbould be possible to give hith-
tew Plasticity to a MeW sueb as Un that does not have a
CU. Utemp. form by alloying it with a metal that would
taxid to thiaresuft. Tbree%Cuwasshowntoproduce
dwdk 97 A. G. Ovy

US~R/~heviistr Ift
Alloys:, y J14
'The 'Webanical. I~roperties PfAlloyd',i-6f the; Cystdm~
Mw"ium-Cadmium;" Ye - M., Savitskly~p-- V` "BaA r0nP
Inst of Gen and Inorg Chem imeni 14. S.rftrnakov,
Acad Sci,USSR
"IZ Ak Nauk SSSR, Otdel Khim Nauk" No 3, PP 392-.397
The vech -properties of annealed.and,tempered Mg-C.d
al.loys',at normal and.at,:high temps were studied for
the 1st time. Mechanical testing of I annealed, alloys
confirmed that they contain M93W,~ MgCd, and MgCd Ao
at~:room temp. Tbe curves.of~mech properties at 2-
and 3500, and tempering beyond that temp showed:no
avidence of the presence of NgCd. MgCd, therefore,,,
is.not formed by fusion or solid s olln, but. is;a,,:.
typical Kurnakov co=rd. 1-%5d, MgCd) and,MgC43
form considerable regions of solid solns:and are
distinguished from the solid solns from which they
~~e "foi-med. by their higher plasticity and, lovrer~
hardness.

Measurement Of lluternal pressures orivinfited In PolYmOrPhous
VE. 51. Savitski a. (C. R.,
J trietzils, on heating. i amfi~V F. Terckhov.
Acad. Sci. U.R.S.S., 1952, 87. 787--~789).-Samples (cylindrical
specimens Ii mm. diam., 30 rum. long) of Armco Fe and Mit are
veloped
heated inan apparatus which measures the internal stressesde
in them. 'rite results are represented in form of internal stress-tertip.
diagrams. They are in agreement with the change of mechanical
aterials on beating. and polymorphic changes
properties of tbese m, ,p,.,cur es-d,uThe
are easily identiliable on tbC itit.CM.11 StTC,5S-tCY
xceed 0.45, k .. to
internal stress" in Arinco I e do not e,
small volume cban;vs but in Mit they reach the value of 50 kg./rnm.*
at about 95W.
S.K. Ltcuo%viqz.-~

SAVITSKEYI Ye. M.
(Inst. Gen and Inorg. Chem im. 11. S. Kurnakov, Moscow)
"The Dependence of the Mechanical properties of metals on Tbmperature in connection
with their crystal structure." Dokl. Akad. Nauk SSSR, 89, 85-88, 1953.
For pure metals the change of mech. properties with temp, depends on how much
their crystal structure is affected by temp. changes. From this point of view pure meta li
can be divided into 3 groups. (1) Metals for which temp. chaanges do not result in a
change of crystal structure. For these metals phys. properties show no drastic changes
witli temp,, and the changes are eontinuous. All inonomorphic MethIs with cubic space
lattice structures belorg to this group. In with its dense tetragonal lattice structure
can included. (2) Methla that at room temp. have poor plasticity but develop newjr slip-
planes when heated. Me plasticity of these metals is greatly increased in certain temp.
ranges but the changes allo are continuous. All nomomorphic methlswith hexagonal
lattice structure belono to this group. The drastic increase of plasticity of such metalt
at elevated temps, can be demonstrated particularly well for Mg at temps. between 300 and.
600" .~ Zn and Cd behave much like Mg. Information on many other methos with hexagonal
lattices is lacking. ~~this with rhombohedral and orthorho&Dic lattices might behavein
the same man. ner., but information on them is lacking. (3) P-Uotropic motals. For these
metals ten~p_. changes are accompanied by changes in the crystal stracture. The resulting.
changes in the phys. properties are severe and discrete. They are most pronounced when
the lattice structure changes from one that is unfavorable to plasticity to one that en-'
hances plastic deformation. Me high temp. forms of most of the allotrophic methis are oi
the cubic space lattice type. As a rale, therefore, the kighest-temp. forms of an
allotropic metal must be the most plastic. 7-1h rule can be used; (1) to j~je!g the tbs
coIrrect addns. to an alloy to stabIlize its high 0 cUstal stradture: 1196
best temps for hot-working Of allotropic Metalb; ~Ifto Verify that the high vWWMMW
xU temp forms of allotropic metals must be of the cubic type, and by the saw token., to
dot. the crystal structures at h#~h .temps for those that have not been investizated.

SRV
ffSKIY,
.,
z
~so
f liot
of (empersture on mic"ed-prolieftTe
t-% and cerium F. INL %xinkly sit) V
Fi Tir khowl:

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.
I rinrie.: - Ch-u-n- At
lff"EaT - (;e".:
b

7vauk
kikit Detsical4w, Mad
ra
7
Kbint. 1955,

Iec . timptrties of Li and Cc wits
of tculp.
itpect to liarditess tewsile contraction lit'
Static coullifeuione and cliange itt tioss Section W a s
peamerl
under Witsioti, at 2"Xl* fUr IAL.JIRI ~'O-JAIG' for Ce; "Poly.
~~Isfoilnatiogl r-joig's tire ac 500- (4n* for Lt and
Cc.

quit -1591* G,r Ce.
The rc,ults ill"Wit gratillizilly, itidi,:ate!
Illat the title cmlverain~ Ow gr,-.Ite-st I'Lt"tidly.if Ugh-UnIp.
k
inuilifie-ali"11:t of polpoorlillie Int-lal., 6 wrt,ct (S.. Vv
bidy
91), 8501353); C.A. 45,
~:K.-LtL.41 ~
7.,

-rrv t L -ON It

Effkt of feniperiture "'inechanical ~ropw4fa ot ger.
manium., R. Ikif. Sav*
idLikg and V. F.. Terekhova (N. S.
-
7
'
Kurnakov -TUNT-
73
en
~1norg. Chern., Moscow
)

tov.- A W. Rauk S_S.S.R.~ Inst.
Redkikk Eksmm
Obsbehef. i
Neerg.'. Kbim.- 1955, No. 2, 165-GO.-Irardness,
sure, were
nd. relative shrink
sive strength, a age under pmw
interval from 20* to 950'.- Above
detd. for Ge in the *tcnil),

900' ',
-theordinartly brittle-metal becomes capable of tic
plas
-3 fold
deformation. A 2 -increase of hardness takes I
P ace
i lu'Ct near its m-pw. -The pljenomenon can be explained by
the appearance of ability toward plaitic defonnation.-
M. apoff

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Engineer
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Card 1/1, Pub. 41-41/21
Author : Savitskiy, Ye. 14. and Tylkina, 114. A., Moscow

Title : The effect of temperature on the plasticity and resistance to
deformation of commercial titanium
Periodical Izv. AN SSSR, Otd. Tekh. Nauk 4, 53-57, Apr 55,
Abstract Presents the results of an experimental determination of plas-
ticity and resistance to deformation at various temperatures and
under various stresses of commercial carbon-free titanium and of
titanium with an 0.5-0.8% carbon content. The presence of carbon
within this range was found to increase the strength and decrease
the plasticity at temperatures of 2o-6ooO. it was found that
carbon does not decrease the plasticity of titanium at tempera-
tures of 700-8000 and over and permits the hot deformation of
titanium under.lcw stresses. Graphs. Four USSR references.
Institution
Submitted. February 11, 1955

SOV/1 3 7- 57- !- 1489
Translation frorn: Referativnyy zhurnal~ I'Vetallurgiya, 1957, Nr 1, p 198 (USSR)
AUTHORS. Savitskiy, Ye. M., Tylkinla, NI. A,
TITLE: Rhenium and Its Alloys (Reniy i yego splavy)
PERIODICAL: V kn Is sledovaniya po zha roprochnyrn s plavam Moscow-, AN
SSSR, 1956, pp 33-47
ABSTRACT: The authors investigated the structure and properties of alloys of
Re with Mo at different temperatures. The specimens were prepared
by the cermet method. Specimens.of cast Re were obtained by melt-
ing briquettes prepared from powder in an electric-arc furnace in an
Ar atmosphere, at 200-mm Hg pressure, Introduction of 1, 3, 5, 10,
25, and 50 weight-jo Re does not cause any changes in the micro-
structure; the Re dissolves in the Mo, and all these alloys have a
single-phase structure of a substitution- type solid solution. Thealloy
with 75% Re is an intermetallic compound, expressed by the stoichiorne-
tric ratio MoZRe3 . With an increase in Re content up to 25- 50% the
hardness of the alloy increases; the alloy with 7516 by weight of Re has
the maximum hardness equal to I 12 0 ke /mm2. 'A lowering of the tem-.
Card 1/2 perature to 1940C brings about an increase in hardness;. raising the

SOV/1 3 7- 57-1-1489
RheniUm and Its Alloys
temperature causes a decrease in hardness. A 901/o Re alloy with a 550-kg/mm?-
hardness at room temperatUre maintains a 390-340 kg/mm?- hardness in the 400-
800o temperature range and 220 kg/mm at 11500. Alt specimens except the 75
Re alloy proyed fairly ductile. Their compressive ab > 200 kg/mm2. At 10000,
all alloys exhibited fair dUCti_lity.e.XCCpt for the 757a Re alloy which disintegrated
into powder. I The 907o Re alloy possesses good ductility both at low and at
elevated temperatures. In order to establish whether this alloy can be employed
as a heat-resistant material, it should be tested for its stress-rupture properties.
A vast amount of material on the physical and mechanical properties of Re is s et
forth in this work-, phase diagrams of alloys-of Re with W, Fe, Co, Cr, M 'o, and
Ni, microstructures of cast Re-Mo alloys, and curves of their hardness and
ductility at different temperatures are given. The authors also touched on the
problems of the use of Re in 'the national economy.
Ye. K~
Card 2/2

137-58-1-1909
Translation from~ Referativnyy zhurnal, Metallurgiya, 1958, Nr 1, p 256 (USSR)
AUTHORS: Savitskiy, Ye.M., Baron, V.V.
TITLE: The Hardness and Ductility of Molybdenum-base Alloys
(Tverdost' i plastichnost' splavov, na osnove molibdena)
PERIODICAL- V sb,,. Prochnost' metallov, Moscow, AN SSSR, 1956, pp 144-161
ABSTRACT: An investigation is made into the properties and microstructure
of cast Mo alloys with B, Si, Ti, V, Cr, Zr, Nb, Ta, and W added
in quantities of 10 and 20 percent, and also of alloys containing UP,
to 0.5 percent Al and up to 0.2 percent'G. The specimens were
smelted in 'an electric arc furnace in an Ar atmosphere. Hardness
(H) was measured at room and elevated (11500) temperature, while
the ductility of the alloys Was determined by upsetting specimens
in a press. The H of Mo at 200. is increased 3-4 Itimes by additions
of B, Si and Zr. A considerable increase in H is observed On in-
troduction of l5percent Cr and I percent B. Additions of 1-20
percent W do not increase the H of Mo. An insignificant increase
in H is observed when V, Nb, and Ti, (Ti+ I percent B) is added
to Mo. At ~11500 , the greatest increase in H is observed on ad-
Card I /Z dition of B, Si, and Zr to Mo. V, Ta, and Nb also significantly

137-58-1-1909
The Hardness and Ductility of Molybdenum-Base Alloys
increase the strength of Mo at 11500 ~ The least effect is caused by Ti and W.
At 11500 the reduction of H is greatest in alloys containing B, Si, Zr, V,
and Ta when the content of these elements is up to 10 percent, when the Nb and
Cr content is up to 5 percent, and with W up to 20 percent. The alloy contain
ing Ti has the greatest softening effect. Addition of K > 0.2 percent to Mo
causes a pronounced reduction in the ductility of Mo, and when there is > 5
percent B, the alloys become embrittlIed. The ductility of an Mo-,Si alloy drops
sharply when the Si content exceeds 0.32 percent, and it is zero at 3.5 percent
Si. Alloys containing up to 5 percent Ti will take deformation without the
appearance of cracks, but higher Ti content (20 percent) renders them brittle.
The ductility of alloys diminishes with increasing Cr content (over 0.2 percent
to 5 percent Cr), but beyond that it shows little change, while as Nb and Ta
increase to 5 percent it increases, after which it undergoes a pronounced
drop and is 5 percent at 20 percent Nb, and Z4 percent. at 10 percent Ta.
Specimens containing 15-20 percent V fail under compression. Mo-W alloys
will undergo 20 percent deformation without cracks (at 10, percent W and I
percent 13), Bibliography:, 16 references.
Ye.K.
Alloys--EDrdna_36' I!. AU*YS___DuatiIi-ty -3. _k1loya-Vdarostructure
Al-loys--Froperties
Card 2/2

V
USSR Structure of Deformed Materials. E-8
Abs Jour Ref Zhur - Fizika, No It, 1957, 110 9399
Author vitLkly, Tlylkina, M.A., Turanskaya, A.N.'
Inst None
Title Investigation of the Recrystallization of Titanium and of
its Alloys (I. Diagrams of Recrystallization of Titanilam)-
Orig Pub Izv. AN SSSR, Otd. tekhn. n., 1956, No 7, 111-114
Abstract The method of microstructure and X-ray investigation was
used to plot volume diagrams for crystallization: (1) For
titanium lodide,I at cold rolling and annealing in the in-
terval from 500 -- 13000. (2) For arc7melted magnesium
thermic titanium alloy VT1 -- D of type I in cold defor-
mation by compression and annealing at 500 -_ 14000 and of
type II in hot deformation by dynamic compressioa:in the
range 600 -- 13000 (a) with subsequent annealing,and (b)
with subsequent annealing, corresponding to the forging
temperature. (3) For calcium-hydride metal-ceramic tita-
Card 1/2

USSR / Structure of Deformed Materials.
Abs Jour Ref Zhur Fizika, No 4, 1957, No 9399
Abstract nium of type II at hot rolling in the range from 500
IPOOo (a) without annealing and (b) with annealing. It was
established that owing to the presence of polymorfism and o-
wing to the different ability of the D~and(fmodifications to
grow grains, each diagram can be considered so to speak as
of consisting of two diagrMs, corresponding to the tempera-
ture regions of the 2 modifications of Ti. 'The character of
the change in the microstructtire of titanium as a function
of the deformation and heating conditions was shown. The
start of recrystallization takes place in titanium iodide at
a 50% deformation and 5000, at a 5% deformation and 6000 and
in the caae of magnesiurx-thermic titanium the admixtures in-
creaae somewhat.the recr tallization temperature. In the
51s
region of small deformations, from 2.5 to 5%, there exists,
in theq region a recrystallization threshold, which is absent
1rom the~,-reglon of the diagram.
Card 2/2

r, CASV 1410PI, DvAeLl
el;
th k

J
Category USSRISol.~l State Yiiysics Mechanical Properties of Crystals and E-9
Polycrystalline Compounds
Abs Jour Ref Zhur Fiztkal No 2, 1957 No 3950
kat.h.-r _SavitsIAy. ]a___14_, Baron- Vv.-
Dm_-titute of Metallurgy, Academy of Sciences USSR.
T i t1'. e Concer_~A-:!,g the Additiveness of Mechanical Properties of Metallic Alloys
and Mixtures.
~.r ig Bab izv, Se kt-~.'ra f i 7 -kbJjp. aria liza IONKh AN SSSR) 1956,
27, 86-96
ystems 149-Si., Mg-Ge.. Cu-Si, Al-Cu, Ni-Si, and Co-S
Abstxact, Using the s, i as ex-
amplesJ, it is show,!:, that the meeban-Jeal properties of tvo-phase metallic
alloy-mixtures depend substantially on the mutual distribution of the
structure of components in these mixtures. The presence of a soft com--,
ponent (for example ', a eutectic .component), distributed over the boln-
daries of the s-,lid phase, causes a sharp reduction inthe hardness of the
FLI-10Y. No additive dependence of the'properties on the composition is
observed i-ra this case. If the soft component is located in the alloy in
the form of individual inclusions and if the structure is in general-,,.-
broken up- the chs-racter of the dependence of the properties onthe
Card, 1/2

Cat r Y USSFIScl 1 State Phyci cs MechaxnAcal Properties of Crystals and E-9
Polycrysta" Ixe Comp:wcds
Abs Jcux Ref Zhur- - Fizika, No 2, 19157 No 3950
compos t 1 1 scIcsP:!- tc ndditive. Such a distribut,ion of the comparients
can be Lf t'~-.ere J.s a sma-'Ll difference in their melting points
by hct deformetion of cast alloys; if the dif -
fere:ace the m-~ilt~vg temperatures is considerable (AI-Si, Mg-Si, CU-Si)"
the metal -ci-,~nmJc metbod I.s wrf, eff,~ctive, The mechani cal. properties
or tl~~7- C -A-I tkj,]~~Vs at higher temperatures approach additiveness to a
to the cat-~:r-g softendng of th
e Cu-AI2 compound.
-Zn
lzi. scl-,i:se'! based co. the Mg-M) Nig 2 and, NIg-Zr5compounds, the
hard--ez--'~ 2--inearly with the composition at ordinary and high
;-1/2

,,SA.VITSKIT, Y&vgp hmq qvich; AGEYEV. N.V*, otvatstvanny7 redaktor:
MIMLISON3 Bi., a lator izdatelstva; USELEVA, A.A, tekhni-
cheakiy redaktor.
[Effect of temperature on mechanical properties of metals and
alloys] Vliianie temperaturr na mekhanicheskie evoistva metal-
i splavov. Moskva, lz-d--v,*- Akad,,nauk SSSR, 1957. 294 P
(MIRA 1;:6)
1. Chlon-korrespondent AN SSSR (for Agerev. NT T-j)
(Metals, Effect of'tomperature on)

01

Translation from: Referativnyy zhurnal, Metallurgiya, 1058, Nr 2, p 278 (USSR)
AUTHORS: Savitskiy,. Ye.M., Terekhova, V.F.
T ITI, E The Influence of Temperature on the Mechanical Properties of
Cobalt (Vliyaniye temperatury na me kha niches kiye svoystva
koba I Ita)
PERIODICAL: Tr. In-ta metallurgii., AN SSSR, 1957, N'r 1. pp 153- 157
ABSTRACT: . A study was made of the hardness, strength,, and plastic
properties of Co under tensile and compIressive stresses, also
of its ak, at temperatures of 20- 12000,C.* The specimens were
prepared by remelting a grade K-2 cobalt in a high-frequency
furnace, whence it was suction-drawn into porcelain tubes!l I-
12 mm in diameter. The hardness wIas measured in the 50-1000
range by means of a "pobedit" cone loaded with an indentation
force of 100 kg. Static compression was exerted in a hydraulic
press until the first cracks'appeared. Specimens 3 mm. in di-
ameterwere tensile-tested in a Gagarin testing machine. The ak
value was detern-iined for specimens 10 mrn in diameter bearing
circular notches 2 mrn deep. It was found that the rate of de-
Ca rd 112 clrease in Co hardness from 187 kg/mm2 (for temperatures up

137-58-2-4224
The Influence of Temperature on the &1~6chanicaL Properties of Cobalt
to 200) to 15 kg/mm?- (at 11000) abruptly steepened inthe 300-4500 range.
Under compression, 47bdeclined moderately. (up to 4500), then (in the region
of 13-Co) it increased noticeably, accompanied by a change from brittle to
ductile fracture. The magnitude of dropped from 13 kg/rnm2 at 200 to
IAkg/mrnZ at 800~, (5 increased by Reduction in area (necking).111-
creased until the ternperatUre reached 4000, but then diminished as the temp-
erature rose further. The ak-versus -temperature curve had two maxima, at 350o
&:5000,-.with,a. min., at. 4000.-. A hypothesis is advanced to the effect that the
abrupt change in the mechanical properties of the Co in the 350-450O.tempe,r-
ature range is. linked to its polymorphous transformation.
Yu.L..
1,roFerties-Temperature effects
Ca rd 2/2

L
137-1957-1-2--7 5299
Translation from: Referativnyy zhurnal, Metallurgiya, 1057, Nr 12, p 334 (USSR)
AUTHORS: Savitskiy, Ye. M., Tylkina, M. A.
TITLE: Mechanical Properties of Cast Rhenium (Mekhanicheskiye
svoystva Litogo reniya)
PERIODICAL: ,Tr. In-ta metallurgii. AN SSS,R, 1957, Nr 1, pp 158-161
ABSTRACT: Castirigs of Re to be investigated were obtained by melting
sintered powdered metal in an argon-arc furnace. Hardness
tests, conducted in the temperature range between -1940 and
+ 11500 , showed thatIHk varies from 400 kg/MMZ to 134 kg/mm?-,
respectively. Plasticity was determined at ZOO and 10000, At
ZOO and a compressive (57 of ZOO kg/MM2 , the compression was
25-30 percent. At 10000 tN compression was 60 percent, Cold
working increases the hardness by approximately 80 percent.
Recrystallization begins at approximately 1500c).
Bibliography- 7 references.
P~ N.,
Card 1/1 1, iUienium castings-Mechanical properties-Test results

so Vj/ I Z4-58-4-4851
Translation from: Referativnyy zhurnal, Mekhanika, 1958, Nr4, p 163(USSR)
AUTHORS: Savitskiy, Ye, M. Terekhova, V. F.
-----------
T IT LE: Temperature Effect Upon Mechanical Properties of Alkaline-
earth Metals (VIiyaniye temperatury na meklianicheskiye
svoyst-,.-a shchelochnozemel'nvkh metallov)
PERIODICAL: Tr. In-ta metallurgii. AN SSSR, 1957, Nr 1, pp 162-169
ABSTRACT: Experimental investigations as to the effect of temperature
on the hardness, strength, and ductility under tension were
performed on specimens of metallic macnesium, calcium,
strontium, and barium. Experiments were carried,out in an
atmosphere of argon on specially constructed testing installa-
tions suitable for samples of limited dimensions. The results
showed that the samples investigated were graded in the follow-
ing order according to decreasing hardness and strength and
increasing ductility: magnesium, calcium, strontium, and
barium. With an increase in temperature all of the metals
softened quickly and at 500-5500C the strength and hardness
became comparable.
Card 1/1 1. Alkaline earths_-~lechanical properties From the
2. Alkaline earths--Temperature effects

1 3T-58-5- 10599
Translation from: Referativnyy zhurnal, I'vietallurgiya,, 1958, N r 5, p 248 IUSSR)
A UTHORS: Savitskliy, Ye. hl. , Trapeznikov,. V.A.
TITLE: Evaluating the Transition of Chromium From the Brittle to the
Ductile State (K voprosu ob otsenke perekhoda khrorna iz khrup-
kogo sostoyaniva v plastichnoye)
PERIODICAL: V sb. Issled. To zharoprochn.. splavam. Vol Z. Mo5co-.,
Al~ SSSR, 1957. pp 141-147
ABSTRACT: A study is made of the possibility of determing the tempera
ture of Cr transition from the brittle to the ductile, state by
static testing for compress,-on along a single axis and by meas-
urement, of ha rdness. A design of a device for ho*. tests for
static monoaxial compression is presented. The, experiments
were run with electrolytic Cr, reduced in. a current of dry and
purified Hz and then resmelted in a current of tec'hnica I A r in
an induction furnace. Experiments were also run wish industrial
aluminothermic Cr, resmelted in similar fashion in a current.
of technical Ar. It is established that in an Iinterval ran'aing from
room temperature to 2500C for electrolytic Cr and to.3000 for.
Card 1/2 aluminothermic Cr, the ductility (D) changes insignificantly,

137-58-5-10599
Evaluating the Transition of (cont.
and in this temperature interval Gr displays brittle failure (F). At tempera -
tures of A/2500 and 3000, depending upon the degree of purity, Cr reveals a
sharp transition from a region of brittleness to a state of ductility, terminat-,
ing at about 4000, after which a gradual smooth rise in D is observed and the
metal exhibits ductile F. It is shown that the purer the Cr and the higher the
temperature and lower the time rate of elongation applied to the metal, the
greater its D a,nd thelower the temperature of transition from the brittle to
the plastic state. Hardness tests showed that the hardness method also-affords
a fairly precise determination of the temperature at which the transition of Cr
to the region of ductile F terminates and an evaluation of the influence of the
level of purity of the metal, upon its D on heating.
V.N.
1. Chromium--Phase studies 2. Temperature--Determination
Ca rd 2/2

sov/137-58-7-1 -59- 5 1i-1
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, Nr7, p289(USSR)
AUTHORS: Savitskiy, Ye.M. Terekhova, V. F.
TITLE: Investigation of the Mechanical Properties and Construction of
the Diagram of the Recrystallization of Chromium (Issledo-
vaniye nickhanicheskikh svoystv i postroyeniye diagrammy
rekristallizatsii khroma)
PERIODICAL: V sb, Issled. po zharoprochn. splavam, Vol 2. Moscow,
AN SSSR, 1957, pp 148-157
ABSTRACT- The effect of temperature on the hardness, plasticity, and
strength during stretching and compression and also the -a
of Cr of various a rades of purity, namely, hydride (98. 50/0
0
aluminothermic (98, 90/6) and electrolytic i,99, 5 /6) was inves-
tigated. Aluminothermic Cr has the greate
hardness at
room temperature. Its a- 4 - kF while that of
the electrolytic Gr is 17 kg~mm'12. * 'The critical point of the
brittleness of Cr depends upon its purity. Upon compression
the aluminothermic Cr is transformed from the brittle state
0
into the malleable at 300 C; the electrolytic Cy is similarly
0
Ga rd 112 transformed at 200-250 Upon a rise of temperature Cr

SOV/137-58-7-15957
Investigation of the bdechanical Properties and Construction (cont.
softens considerably. Durin8 the transition into the plastic state a certain
0
increase in hardness is observed in Gr of all types at 350-450 , At 10000
electrolytic Cr subjected to monoaxial compression can withstand a single-
0 0
stroke 90 7o upsetting Without failure. In the 500 to 700, range impact
specimens without a notch do not break but bend plactically. In this teM -
perature range Cr can be worked by pressure. A specific characteristic
of Cr is its increase in strength with a rise in temperature. This is es-,
pecially true for impure Cr., The O'b of aluminothermic Cr increases
f rom.4. 7 Z~ 200 to ~ 10 at I 100" that of electrolytic Cr f rom 17 at 200 to
0. -ray investigations showed that the increase in the
28 kgmm at 500 X
strength of Cr in the 300-5000 range is not related to, the appearance of a
new crystalline modification of Cr. A diagram of the recrystallization of
Cr, constructed with the help of microstructural and X-ray methods and by
measurement of microhardness, is adduced. Full recrystallization of Cr-
0
occurs at 1020 . The hardness and the ductility of Cr after recrystalliza-
tion do not decrease; the temperature of the transition of Cr fSom. the brittle
into the ductile state upon compression is decreased by 30-50 /0.
1. Chromium--Physical properties 2. Ghromiihna--Grystallizati~on 3.
factors N, K,
Card 2/2

AUTHORS: Shostakovskiy, M.F. Savitskiy, Ya.11. 62-,2-15/20
Kochkin, D.A* , Musa
TITLE: On the Comparative Efficiency of Silicon Alloys.'ifith Copper and
Nickel, Anplicable in Direct Synthesis of Vinylchlorosilanes
(0 s ravnitell noy effektivnosti sple-vov Yremni3a s med' yu i nikelem,
primenyayeuqkh v pryamom sinteze.vinilkhlorsilanov).
PERIODICAL: Izvestiya. AN SSSR OtdeleniyeKhimicheskikhliauk, 1957,iNr 12,

1493-1495 (USSR)
pP
ABSTRACT: In the course of a thorough analysis of the alloy of silicon with
copper (which -mas already previously described) the authors, among
other things, found that the alloy contained 5V/a silicon, )+9;4 cop-
per, and 0.4,56 aluminum. Also silicon alloys were investigated which
contained also other metals such as'chrcmium, manganese, and molyb-
aemmi. In other cases (with the exception of nickel and copper) nega-
tive results were obtained. IFrom the result of the synthesis (see
table) it may be seen that the silicon-nickel alloy is more active
(when vinylchlorc~Llanes are obtained by direct synthesis). it was
further shown that the silicon-nick-el alloy (nickel content 15%)
Card 1/2 must be considered to-be the most suitable. There are I table, and

hTJTHOR SAVITSKIY Ye.M~, BARON V.V., IVANOVA K,N, 20-5 -5: 5/67
TITLE Diagram of M;71-ybdenum Recrys tall izat ion.
(Diagramma rekristallizatsii molibdena -Hunsian)
PERIODICAL Doklady Akademii Hauk SSSR,1957,Vol 113, Ir 5,PP 1070-1072(U.S.S.R.)
-Received 7/1957 Reviewed 8/1957
ABSTRACT Apart from other factors, the size of grain is known to influen-
ce the mechanical properties of metals. in the case of molyb-
denum this manifests itself with particular clearness. I britt-
le and coarse-grained structure can be rendered more fine and
uniform by a suitably selected heat treatment. In this way'the
material becomes more plastic and is better suited for cold treat-
ment. Therefore the Betting up of a recrystallization diagram for
molybdenum, which contains the size of grain, degree of degree of
deformation, and annealing temperature, is of particular interest.
As hitherto this problem had been but little investigated, the au-
thars carried out therecrystallization of molybdenum of the first
type. In order to obtain a uniform, fine initial structure, the
material was several times forged at from 16oo to 12ooo.The total
degree of deformation amounted to 96%. As a resultof this treat-
ment the very, coarse and uneven structure disappeared. Forging at
low temperatures'led to the formation of texture. After annealing.,..
in the vacuum at 1300 the samples had a. polyhedric fine-grained
structure with an average size of grain of about 22. - 25 . On
Card 1/2 the strength of these results it may be assumed that the hot for-

"Recrys tall Lza LA on. D.Lagrams, of.' T-Ltan[wm In(! Its A-11uys 11 with TYLKINA, M. A.) and
TURWISIVi.YA, A. N., Titan i yegcj splalty; metaullurwiya- I metallovedeniye (Titanium
and Its Alloys; Metallurgy and Physical Metallurgy), Moscow, Izd-vo AN SSSR,
1958. P 3.)
(Institute of Metallurgy, USSR Acad. Sci.)
"Mechanical Properties of Tlitanium of Various Degrees of Impurity," p 68., Ibid.
(co-authors same as above).

SAVITSMY Ye. M.
18(2) NOR 11 - ABSTRAM A60-1
Akodfttjr& nouk&MR. InStItut sstsllur$U
Ilov~4#nljr* (Titanium and Its
Titan I yeso oplavy; notit1juralls I meta
Aaxoysl Metallurgy and thy*14&1 Metallurgy) Moscow* 114-To AN
SM. 1958. 209 P. 4,000 copies Printed-
Peep. Xd.i N.Y. Agoyev, Corresponding member, OW Academy of solonsess
Ad. of Publishing Housso V.3. flaheanikov$ Tech. fid.1 A.A. 11selovs.
WOUKTIONs This book. of which a Phase I Loplottation (SOT/1200)
has been prepared, to 6 collection or sclantiflo papers devoted to
the study of titanium and its alloys frcs three owls points of vIONO
phystoda ftstanwaw, forming, and woldins. sposial problems In-
aill
V"tl&stod InSIVOO 4trw*UUV1 changes occurring &Urlfl$ WOI"nS# 440-
Pak I Yhysicalmet toreasallom of UW content or hareftl Comes. development At In"@-
trial wommin of rolums, WA oxidation as ve"eme 24mverateres.
~Savitski -A N'" Tuf~fiikFy';W7
Y, Ye Me, ~M.A. Tylkiiias . 0,
Rnstitute.~,Of: Metal-...,
1urgY
USSR Academy,of Sciences)- Recrystallization-,Dia-grams of,,:
Titaniibm and Its Alloys
:83
-The aim of this investigation, conducted in 1954-55, was to
study the process of,recrystalliz
ation of titanium of various de-
grdes of purity and of its alloys under conditions of various
types of deformation and to construct two types of three-dimen-
sional diagrams of the recrystallization process. Type I diagrams
show the relationship between grain size, the degree of,cold work-''
ing, and the temperature of~subsequent annealing, and can be used
4" establishing correct conditions for the annealing of Semiftnighpd

Titanium and Its Alloys (Cont.) AB-1
and finished products. Type II diagrams illustrate the relation-
ship between grain size, degree of hot deformation, and temperature
of hot deformation; they are useful in establishing optimum condi-
tions for the forming of metals and for obtaining the desired pro-
.perties,in semifinished and finished products. Before the present
investigation no such diagrams had been published. A study was
made of the recrystallization of three types of pure titanium:
(1) iodide-derived; ~fl magnesium-reducea_(type VT-lD),, melted in
an are furnace; and 3 CaH2-reduced., sintered (type IMP-11). Simi-
lar studies were made for VT-2 titanium-aluminum-chromium alloy and
for IMP-3 alloy (CaH2-reduced "'titanium with an addition of chromium.
Diagrams of Types I and II for recrystallization under conditions,
of rolling and forging were established by methods of microscople
and x-ray analysis. Conclusions. 1) The following recrystallIza-
tion diagrams were constructeT.--a) Type I for Iodide-derived titanium
with deformation by means of rolling; b) Type I, with deformation
by static compression, and Type II, with deformation by,smith forg-
ing, for technical Mg-reduced, fused, and hotrolled titanium (type
VT-lD);'e) Type II,.with deformation by smith forging, fQr VT-2 al-
loy; d) Type II, with deformation by hot rolling,, for IMP-1 titanium;
Card 10/43

Titan~.um and Its Alloys (cont.) AB-1
e) Type II, with deformation by hot rolling' for IMP-3 alloy. 2)
Because of the polymorphous character'of titanium and the different
capacities of the alpha and beta forms for grain growth, the re-
crystallization diagram should be thought of as consisting of '%'-Iwo
parts corresponding to the temperature ranges in which the alpha
and.beta forms exist. The alpha phase of,T1 is characterized by a
finegrained polyhedral structure, and Insensitivity to the rate of
cooling after annealing, and the existence of a critical grain size
after cold deformation of 2.5-7 percent. The beta modification is
distinguished by a large grain size and high sensitivity to the cool-
Ing rate, a consequence of which Is the different shape and size of
the grains in the hexagonal modification (o~') appearing as a result
of the polymorphous transformation of beta titanium in cooling.
5) In iodide-derived and commercial titanium the boundary contours
of the beta grains are preserved, no matter what the cooling rate,
and can be destroyed only by deformation in the alpha phase. The
contours of the beta grains.in CaH -derived Ti and in VT-2 alloy
2
can be preserved only by rapid cooling. 4) In thestable tempera-
ture range of the beta phase there were no indications of a re-
crystallization threshold or a maximum corresponding to critical
degrees of deformation. This is probably due to the fact that
Card 11/43

Titanium and Its Alloys (Coni.) AB-1
structural changes caused by small plastic deformations in the
alpha temperature range are erased by the structural changes de-
veloping as a result of the polymorphous transforMationzr.,z:-_tj3
in titanium. 5) The optimum annealing temperature for obtaining
alpha titanium of polyhedral structure falls within:the 650-8500C
range, depending on the purity of the metal and the extent of the
previous deformation. More exact indications As regards the an-
.nealing temperature regime for each degree of deformation can be
obtained by referring to the recrystalliz&tion diagrams. 6) Under
conditions of smith forging and rolling at the rate of 0.5 m/sec~,
recrystallization in commercial titanium does not hkve time to go
to completion. However, recrystallization may still set in with
subsequent heating, or during the cooling of large blanks, or in
further working of the still hot material. For this reason, the
danger of the development of a coarse-grained structure, especially
in the case of small deformatlons, should always be kept in mind.
There are 22 figures, 5 tables, and 11 references (8 Soviet, 1 Eng-
ligh, 1 German, and 1 Japanese).
Card 12/43

Titanium,and Its Alloys (Cont.) AB-1
Savitskiy.0 Ye.M., M.A. TylUna, A.N. Turanskaya (Institute of Metal-
1 ~~W,~~demy of Sciende's-)-- Mechanical Properties of Titanium
of Various Degrees of Purity 68
The aim of this.investigation, conducted in 1954-55, was to de-
termine the mechanical properties of titanium produced by~various
methods and studied under different.conditions of temperature
and stress. The materials tested were:jl) Iodide-derived Ti;
(2) sintered Mg-reduced-Ti; (3) Mg-redticed Ti melted in an"in-
duction furnace In graphite crucibles (0-5-0.8 percent C); (4) Mg-
reduced Ti melted in an are furnace with tun$sten electrodes
(VT-lD commercial T1, contaminated with W); (5) sintered CaH2-
reduced Ti; (6) cast VT-2 Ti-base alloy with additions of 2--3
percent of Cr and 1-2 percent of Al; (71 sintered alloy of Ca%
reduced Ti base, with addition-of Cr. Tests were made for them
following mechanical properties: hardness, strength, and ductibi-
lity under compression and tension, and impact toughness. The.ef-
feet of temperature on the properties was tested in the range ex-
tending from -1960 to +11000 C in vacuum, argon, and air. Cool-
ing to _1960 was accomplished with the,use of liquid nitrogen.
Hardness was deter-mined by producing an Indentation with a pobedite
Card 13/43

Titanium and Its Alloys (cont.) AB-1
cone with a load of 100 kg,(for iodide-derived TI, 15 kg) in a
temperature range of -1960 to +10000 C (in a current of argon when
the specimens were heated above 400' C). Conclusions. 1) The de-
gree of purity as determined by the method of prepa-r=ng titanium
materially affects the mechanical properties of the metal. Iodide
derived Ti,of very high purity exhibits considerable ductibility (de-
formation of up to 951gercent in cold rolling) and withstands bend-
ing at an angle of.,/ 00 without breaking, even at -1960. I~s hard-
ness was.the lowest of any of the materials tested:.132 kg/mm . con-
taminatiop of the metal greatl_y increases its hardness (from 132 to
330 kgf/=~ ). and its strength from 25 to 100 ka/mm?), as a result bf
the decrease in ductility and impact toughness. The relative hard-
nesb at 200. C of five of the materials tested is shown in the follow-
Ing sequence.(materials arranged in Ascending order of hardness):
Iodide titanium; VT-lD commercial TI, Mg-reduced (W-contaminated);
CaH2-reduced Ti, Mg-reduced Ti, melted in graphite crucibles (0-5-W.
percent); VT-2 alloy. .Differences In the properties of Ti contain-
Ing 0.53-0-82 percent of C were practically undetectable. 2) Tita-
nium is highly sensitive to the rate of deformation. An increase in
the rate causes a sharp drop in ductility characteristics. 3) Lower-
in the temperature to -1960 increases the strength and decreases,
Card 14/43

TI tanium and Its Alloys (Cont.) AB-1
the ductility of all types of titanium. An increase.in temperature
brings about,a rather intensive softening and a loss In strength
of Ti of all types. Above 6000 the difference in the mechanical
properties of all types of Ti evens out, and the effect of impuri-
ties levels off. In deformation at a low rate of speed in the neigh-
borhood of 700* the strength-reducing effect of recrystallization
also begins to be seen. After a polymorphous transformation In the
beta phase, titanium of all,.types becomes Mery ductile, having an
extremely low resistance to deformation. 4) The mechanical pro-
perties are a sensitive indicator of structural changes taking
place in titanium as a result of heat treatment. Heating of.titanium
of all types.at temperatures above 1000' always leads to a preser-
vation of beta-phase grain contours after cooling and transition
to the alpha phase and considerably lowers the mechanical properties,
especially ductility. Heating regimes in deformation and annealing
were established, making it possible to obtain an alpha titanium
of fine-grained polyhedral structure having optimum mechanical pro-
perties. There are 10 figures, 3 tables, and 14 references (8 So-
viet and 6 English).
Card 15/ 43

IPA
I
!W. a
KEN
A3
3v-j "2
.'If Tq;j 3 H! t Z. all
Ala
I ii H j i Ail\
HU
Hip I
H;1
au
41
32 9
9
A.; v o zi 0 1
:9
I-A lei H
LO 0.: a INI

AUTHORS: f1.) bocLor of Chemical Science.1 5 o - 2 9
Savitskiz
Z__Ye__-
_
__,.
Terekhova, V. r., Candidate of Technical Sciences
TITLE: Investiration of the Alloys of flare Metals (Issledovaniye splavov
redkikh metallov)
All-Union Conference (Vsesoyuznoye soveshchaniye)!
PERIODICAL, Vestnik Akademii 114auk SSS,Z, 1950, Nr 2, pp 111-112,
(USSR)
ABSTRACT: On November 18 2o, 1957, an All Union. Conference was called by
the Institute for Metallurgy imeni A. A. Bajkov of the,AN USSR
and the Board for Rare Metals at the Scientific Technical
Cori:aittee of the Cabinet Council of the USSR. The conference was
attended by reprenentatives of scientific research institutes,
universities and industry. Reports on raw material sources of
rare metals and their production in pure state, problems of
scientific investi.-ations of Alloys of rare metals, investi.ation
results of alloys of various systemif~, their physical chemical
properties and industrial application were delivered and discuss-
ed. Serious shortcoritinas hinderin;1 the developnic-tit of research
were pointed oat. Above alli the intensification of the product-
Card 112 ion of pure rare metals was demanded. The determination of the

~Irzvestigation of the Alloys of Rare Metals. 3o-2-42/49
All Union Conference
constants of physical chemical properties of pure rare metals
and their alloys has to be regarded as the least~investiaated
which hinders its rational introduction into political economy.
Also systematical work in this field is carried out insufficient-
ly. There is also a lack of inVormation in this field; no spe-
cial periodical exists. The importance of the ascertainment of
new metals with addition of rare metals for the new technica
was streszed. Researdh work must be considerably extended and
carried out more quickly. For this work also the institutions
of.the AN JSSR and their subsidiaries, the.academie3 of the Re-
publics of the Union, branch institites, universities, and labor-
atories must join. The Institute for Metallurgy was charged
with the coordination of the work. The resolution was also made
Lo carry out the work methodically so as to shorten the necessa-
ry time and to reduce the expenses of research work. Equally the
demand for an own periodical was expressed.
AVAILABLE! Library of Congress
1. Rare metals-Sources 2. Rare metals-Alloys .3. Scientific
Card 2/2 research-Rare metals 4. Metallurgy-USSR 5. Rare metals-
Production

24-58-3-11/38
AUTHORS:Savi-'Uski.7. Ye,L_ Tylkina,_ ?J-,A,, Tsyganova, !,A. (MrDscow)
TITLE: Additions on the Recrysta.-Ilization Tempe.
ral i
lure and on the Mechanical Pro~)erties of Titanium.
(Vliyaniye le-iruyushchikh dobavok na tom eraturu rekristalli-
0
zatsii i meldianichoskiye svoystva ttt.ana5
PERIODIC"AL: Izvestiya Akademii Nauk SSSR-, Otdelenj.ye Telchnicheskikh
Nauk-, 1958, 1-Tr 3, pp 96-103 and 1 plate, (USSR)
ABSTRA(.3T: This paper is a continuation of earlier work of the,
authors and their team on the recrystallization and the
mechanical properties of Ti of various degrees of purity and
of Ti alloys (kefs.1-6).. Reinbach and Nowikot%r (RefL.7) pub-
1!shed preli-mi-nbxy data on the influence of certain additions
(U-0 0
to 196) on the change irt the time required 'to attain com-
-ion of commercial Ti at a giv-en annealing
plete recrystallizat "I-
temperati.Lre; they found that introduction of chromium slows
dovinthe T,-,rocess of recrystallization whilst other admixtures
(C()7 Al, Fe, Ta and Sn) showed almost no influence on the
duration of attaining ,~omDlete recrystallization, In this
paper an attempt is made to classify t-he alloying elements
from the point of vie-w of their influen.-e on the racrystalli-'
zation temperature and the mech~ani~3al properuies whereby these
characteristics are considered as -a fun,-.tion of the character
Card 1/5

24-58-3-11.138
Influence of Allovin:r Additions on- the Recr
.7stalllzation Temperature
--)eries of Titan-Ltuz,
and on the Mechanical Pro.
of the interaction of Ti vrith the alloyin,-:, additions, their
crystal structure and also the temperature of poly-morphous
transformation. The relations published by Bo,3hrar (kef.8)
-and by Kurilekh (Ref,q), interrelating the rezrystallization
temperature of,metals with their fusion temperature, are not
applica'ble to alloys. The complexi-t-Y of diffusion processes,
in solid solutions, the differlin'rr Charactz~r of,.these solut-
3-ons -9rd the presence of second phasez in the alloys are all f ac-
Lors ~which complicate the process of recrysta-I'Lization. One
iraDartant fact'or which has not been taken into consideration
so fj-.r is tile T)resence in metals or alicys of the phenomenon
of polymorphism, in. the view of the authors of this paper,
in metals and alloys. in whirh polymorphous transf ormation
taJ~.es -r)lace, the re cry stall ization temperature should be
closely linked with -the temperature of the polymc-rp-licus
transformation in addition -11-o the in'Lluence of other factors.
that in alloys in which such transformation'
It is obvious L.
t.akes -ulace all t-he recrystallivzation processes are fully
comPleled in the range of existence of lciver tamparature
Card 2/5

Influence of, Alloyiing Additions on the Recrystallization Temperature
and on the Mechanical ProDertkies of Titanium,~
modifications (particularly a modification in Ti) and vill-en
phous transformation is reached,
the temDerature of polymor-
Dhase recrystallization and reconstruction of the crystal
iattice is already proceeding, The experiments were carried
out with an iodide Ti of 99,961/o purity alloyed with additions
of -the following 14 elements. T Nh, Fe. Co, Un, Cr, N ~ C,
e. Re Sn and Boron, addl:t-
0., Al,_ B For each of tl~e alloying
.ions, 4 to 5 alloys viere prepared and the content of each.of
the additions in the alloy was chosen in such a Way that
alloys were obtained which are located in various phase ranges
of the system, namely, alloys possessing uniform a and P
structures, 2.-'-phase a Ll I
+_P or a + chemical compound structures.
The compositions of the alloys are entered in the table on
,P,97. Graphs are included showing the influence of the
annealing temperatLirre on the hardness, the influence of the
alloying additions on the recrystallization temperature, on
the ultimate stren-th. elongation and contraction, it was
found that almost all of the investigated alloying additions
bring about an increase in the recrystallizatiorl temperature.
As re-ards the de-ree of their influence these elements can
C__ C:)
-abdivided into the following three groups: elements which
Card 3/ ~e s

Influence of Alloying Additions on- t-h- Rezrystlalliza--ion Temperature
and on the Mechanical Properties of Titarliuzni,
brin - about a considerable increase in the recrystallization
temperature at low contents of the respectlive element (IT, 0,
Boron, Be, Re and Al); elements which bring about an.
increase in the recrystallisation only if,the content is of
the order of and hi-her (Fe... Cr,, V, Mr,., Sn); elements which
have practically no influence on -the initial recrystallization
temi)erature (Nb and CoY, The following relation was derived
between the recrystallization temperature, T 1 and the tem-
perature of the polymorphous transformation.. T2 I of the
alloy: TI/T For Ti this ratio equals 0.71 for
2 = 0-7 0-9
low alloy alloys,this ratio equals 0.7 0,75 and increases
to 0,,8 - 0.9 with increasing contents of the alloying element.
The alloyin- additions bring about an increase in the tensile
stren-th and hardness,, maximLua values being 92 kglmdL
0 CrB
and RB 105 and a reduc.1-ion in the ductility. The gre at,-
est influence is exerted by elements which bring about a
maxi ri um increase in the recrystallization temnerature and
Card 4/5

24 - 5~,3-7-1 1/ 38
Influence of Allo,-
,rin- Additicn-s on th-e Re_~;r7stailizaticlr. Temperature
and on -the Mechanical Properties of Titanium,
belont-- to the first of the above-raentioned group,, i.e., N, 01,
C., Be, B. The other investi-ated elements have less influence
on incroasinC the strength and for a content of 5/6 these
elements can be classified from the point of view of.increas-,
in- -the stren-th in the following sequence: Cr. CO, lfb~ V,
flifti! Fe and Sn,, The greatest drop in plasticity is observe'd
when introducing Fel, Co and Nb, There are 9 figures, 11
table and 15 referenQes.., of which 10 are Soviet., 4 German and
1 English~
SUBNUTTED: April 1957.
TiUmirix-Mechanical prooArtion 2. Tltanl= alloys--!taarystal-
Card 5/5 liziLtion

78-3 3-37/47
AUTHORS: Savitskiyq Ye. M. Terekhova, V. F.
TITLEt The Phase Diagrams of the Alloys of Lanthanum With Cerium and
Lanthanum With Calcium (Diagrammy sostoyaniya splavov lantana
a tseriyem i lantana s kalltsiyem)
-6-762
PERIODICAL. Zhurnal Neaganicheskoy Khimii )l 95R-V':'1' 31Nr pp-75
(USSR)
ABSTRACTt The phase diagrams of,the Alloys of lanthanum with.ceriumg
and lanthanum with calcium were investigated by thermal, ana-
lysis, and by the determination of microstructurej hardness
and electric resistanceg and the diagrams were constructed,
In the system lanthanum-cerium purest metallic cerium with
97 - 99 e,- purity and lanthanum. with 9895 % purity were used.
Lanthanum and cerium dissolve in a liquid and solid state
and form a diagram with unlimited solubility. In the system
lanthanum.-Calcium the initial metals were molten in a vacuum
under an argon atmosphere. The produced alloys were investi-
gated by the determination of microstructure and the analyses
Card '1/2 showed Thai in a solid state a layer formation is to be

78-3,3-37/47
-The Phase Diagrams of the Alloys of Lanthanum With Cerium and Lanthanum
With Calcium
noticed. The thorough investigation by the microstructure
determination showed that in a solid state more than two
layers occurs The occurrenne of two layers in the alloys can
already be observed at a calcium content of more than
12 -- 15 ',4,- With an -increase in the calcium content to 30-60
the thickness of the outer layer highly increases. By the
chemical analyses, thedetermination of the specific weight
and the hardness of the layers it was found that The upper
layer consists of calcium and the lower one of lanthanum.
The alloys with about ~i d,. calcium consist of a phase of solid
solution. The alloys with 60 - 80 % calcium have three.
layers of which the middle one is of polyhedral structure and
is rich in calcium. The solubility of lanthanum in calcium
and of calcium in lanthanum at an eutectic temperature of
7050C is not higher than'3 5 %. There are 15 figures, 4
tablesq and 8 referencesv 3 of which are Soviet.
ASSOCIATIONg Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(Metallurgical Institute imeni A. A. Baykov
,AS USSR)
SUBMITTEDs ,
June M 1957
Card 2/2

78-3 -3 -38/47
AUTHORS: Savitskiy~ Ye. M~ Baron-, V. V. Tylkina, M. A~
TITLE: The Phase Diagrams and Properties of Gallium and Thallium
Alloys (Diagrammy sostoyaniya i svoystva splavov galliya i
talliya)
PERIODICAL% Zhurnal Neorganicheskoy Khimi.iq -77
')958,v01-3, Nr 3.. pp.763 5
(USSR)
ABSTRACTa The structur6.1 aiid physico-mechanical properties of the alloys
of~rallium,with silicon and germanium in all concentrations as
wail as of gallium with antimony, manganese9 copper and thal-
lium with lanthanum were investigated6 The phase diagram of
gallium with silicon is ofan eutectic type. All- alloys con-
sist of two' phases. Theaddition of
silicon to gallium high.
1y inereases.the.hardness and,the electric resistance of sili-
con~ The phase diagram of gallium and.germanium also is of 'an
. 0
eutectic type. The eutectincomposition melts at 29 C and.has
a gallium content of 99745 4~. All alloys of this system possess
metallilo. conductivity.
Card 1/3 The'structure and the properties of the.allo~* of gallium and

-8-3 3, 38[47
The Phase Diagrams and Properties of Gallium and Thallium Alloys
antimony were examined for hardness, microhardneau, plasti-
0
city,, strength and electric resistance between 20 and 6oo C.
Alloys with 63,59 -- 64,X8 ~ antimony at room temperature
have a maximum eleotric resistance which decreases with a
r4se of temperature This proves that these alloys possess
properties of semiconductors. The structure and the proper-
ties of the alloys of gallium with 50 - 86,,3 % gallium were
exaralned by aiicroatructure,, hardness, strength, microhard-
ness and electric resistance at, temperatures of `20-%WO Co.
The fol Ilowing compounds occur in the alloysi MgGa and Mg Ga
A]Lloys in the domain of the compound MgGa show the highe2t
hardness and the smallest, strangth and plasticity. The system
gall iuw..- P. opper with 15 - 85 ~ gallium was also Investigated
for miprostructure,, hardness, strength,,, microhardness and
electric resistance-The resulis showed.that by the addition
of gallium to copper hardness, strength and electric re-
sistance Increase., but that the plasticity decreases. The
electric resistance of the alloys increases with a rise of
temperature. The phase diagrams.and the properties of the
alloys, of galliwa with grermanium, gallium with silicon and
loys between
gallium with lanthanum.were also infestigated. U
Card 213 silicon and thallium. do not occur. In the system lanthanum~

78-3-3-46/ 47
AUTHORS: Savitskiy, Ye. M. Tylkina, M. A.
TITLEt Alloys,of Rhenium With High-Melting Metals (blo' Ti, Zr., Ta.
Nit Cot Cr, W, Mn) (Splavy reniy*a s.tugoplavkimi metallami
.(140, Ti, Zr, Ta, Ni, Co, Cr, W. Mn))
PERIODICAL: Zhurnal Neorganicheskoy Khimii0958,,Vol,,3, Nr 3,PP.820-836
(USSR)
ABSTRACT: The investigations were performed with different pbysico.-
-chemical methods, especially by the determination of the
,melting point. On the basis of these investigations the
nature of the alloys in the case of the influence of rhenium
upon high-melting metals was determined. The modification
of the hardness, the melting point and the electric re-
sistance in this system'was observed. In the system Ti-Re
a larger solubilit domain of rhenium in 0-titanium was
y
determined. Onthe intro-duction of rhenium the A-phase
of titanium is.stabilized. In general the addition of rhenium.
to titanium increases the thermal.stability. In the system
0
Mo-Re solid solutions occw. At a tempe-Tature of 2570 C an
Card 113 d-phase occurs by peritectic reactions The boundary of the

78-3-3-46/47
Ailoys of Rhenium With High-Melting Metals No, Ti Zr, Ta, Ni, Co, Cr, W,
Lin),
solid solutions of rhenium in molybdenu.m was notexactly de-
termined. In the system Ta-Re in thecase of 60 -,70 ~ rhenium
thecompound Re Ta 2 was determined. On addition of 60 - 80 %
rhenium the all9ye in this system are brittle and breakable.
In the system Co-Re an uninterrupted series of solid solu-
tions with an hexagonal crystal. lattice between oc,--cobalt and
rhenium was determined. In the system Ni-Re solid solutions
of rhenium in nickel (oL,,phase) occur and solid solutions of
nickel in rhenium-( A-phase). The boundary between these two
0
phase domains lies at 1200 C in the case of 40 - 75 %
rhenium. In the system Cr-Re domains of solid solqtions of
rhenium in chromium occur. In the case of 70 - 65 % rhenium
a chemical compound forms which possesses a hardness of
1000 kg/;nm2. A smaller addition of rhenium to chrnmium in-
creases the plasticity.of chromium. In the system Zr-Re two
chemical compounds forms i) In the 0case of,50 % rhenium
ReZr 2,,with a melting point at 1900 C and an hardness of
800 - 1000 kg/mm2l 2) In the case of 70 - 80 % rhenium
Re Zr, wit a melting point at 24000C and an hardness of
1280 kg/mm . Solid solutions of rhenium in A-zirconium
loccur,at up to 15 % rhenium..In the System Un-Re with Lip
Card 2/3 to 5 % rhenium solid solutions occur. On additionof 24,,6 %

78-3-3-46/47
Alloys of Rhenium With Ifigh;.Melting Metals No, Ti, Zr, Tak, Ni, Co, Cr, W,
mn)
rhenium a polymorphous transformation of to Ococcurs, at
7600C. In the system W --Re with 60 %orhenium-a phase of W 2 Re .3
forms, with a melting point at'5007 C. In this system an
6-phase also occurs at 35 '.58 it% as well as solid solu-,
tions of tungsten in rhenium at~15 % rhenium. In all in-
vestigate-d-systems the produced alloys have a lower melting
point than rhenium. There are 17 figures, 6 tables, and 35
references,.12 of which are Soviet.
ASSOCIATION3 Institut metallurgii im. A. A. Baykova, Akademii nauk SSSR'
Moskva
(Moscow Metallurg-ical Institute imeni A. A. Baykov AS USSR)
Card 3/5

sov/78-3-9-22/38
AUTHORS: Savitskiy, Y--. I.Terekho-va,.Y. F., Novikova, 1. A.
TITLE: The Phase Diagram of the Alloys of the System Magnesilam-
Neodymium (Diagramma sostcyaniya splavo-v sistemy magni neodJm)
'PERIODICAL: Zhurnal neorganicheskoy khimii, 1958, Vol 3, Nr 9, pr 2138-2142
(USSR)
ABSTRACT: The thermal analys-,s, the microstructu--e, and.the.determination
of the microhardness were used for the construction of.the
phase diagram.of t1he system magnesium-neodymium. The hardening
method was used for "he determination of the solubility of
neodymium in magnesium-in solid state. Chemical compounds of
neodymium and magnesium exist in the solid solutions of
neodymium in magnesium within the range of 40 60 percents,by
weight neodym1um. Ccnsiderable structural changes of the alloys
4.
occur with an increase of the neodymium content up Uo 1%. if
neodymium is added to magnesium, the hardness is increased and
the mechanical properti-les of the alloys-are improved. The
strength and plasticity .P _,_ S
_1L Un alloys in the system neodymilim
magnesium in the region of the solid scliition on the basis of
Card 1 2 magnesium are Increased rith ri-s-ingneodymium content. At 150

SOV /78-3 -c)-2 2/38
'The Phase Diagram of the Alloys of the System Magne31JUM-Neodymi,=
and 2500C the alloys.of magnesl neody siderably
ium with mium are con
more solid than pure magnesium. The microstructure of them
alloys changes to a great extent in alloys with 10~- neodymium,
they reach the.max--mum dispersion at 25% neodymilim.
There are 4 figures, 2 babies, and 7 references, 4 of which
are So,.riet.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii.nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov, AS USSR)
SUBMITTED: January 21, 19.18
Card 2/2

SOV/24-58-4--6/39
AUTHORS: Baron, V.V., Yefimov, Yu.V.and Savitskiy,
TITLE: The Structure a Ind Properties of Alloys in the.Vanadium-
Molybdenum System (Struktura i svoystva splavov sistemy
vanadiy-molibden)
PERIODICAL: Izvestiya Akademii Nauk SSSR, Otdeleniye Tekhnicheskikh
Nauk, 1958, Nr 4, PP 36 - 40 (USSR)
'ABSTRACT: A vanadium-molybdenum phase diagram has not been published
so far. As Mo and V have the same crystal lattices,
similar atomic diameters and identical electron structures,
it is possible to assume that these two elements form a
continuous series of solid solutions. This assumption has
been confirmed experimentally when measuring the lattice
parameters of powder-metallurgical specimens of V-Mo.
However, cast V-Mc alloys are reported to exhibit a second
phase at between 10 and 60% Mo.
No data on the physical and mechanical properties of these
alloys exist. The authors have carried out an investi-
gation of the structure and properties of V-Mo alloys,
established their melting temperatures and constructed a
phase diagram for them..
Cardl/4 Alumothermal vanadium, containing 95.5% V1 0.% Al~ 0.15FID, Fel

SOV/24-58-4-6/39
The Structure and Properties of Alloys in the Vanadium-Molybdenum
System
6 C, 0.3% Si and a considerable quantity,of oxygen,
0-2~, -containing
and molybdenum in the form of sintered rods,
99.00% Mol) 0.075% C. 0.04% Fe and.traces of Si and W,
served as raw materials. The alloys,were prepared in an
are furnace, provided with an insoluble tungstenelectrode,
in a helium atmosphere. The voltage applied was 60 V
and the current 1 000 A, the electrode diameter being 8 mm.
Bach alloy was remelted four times in order to eYisure Oen
mixing, and each ingot weighed 60 to 70 9- OPectroscopic
analysis of the alloys for impurities showed the.presence
of 0.01% each of Fe. Mn and Si and traces of.Mg and W.
The solidus and liquidus temperatures for alloys of various
comDositions were datermined7and a phase diagram constructed
.(Figure 1),. This shows that all.alloys are solid solutions.
The as-east structures were examined and hardness.values
determined. 'The specimens were f-hen homogenised by
annealing for 10 hours at 11 600 6C in vacuo. The micro.-
structures of the homoSenised specimens were also examined
and hardness, mi crohardness,,plasticity under a compressive.:
Card2/4- load and electrical resistance determined. Hardness was

SOV/24-58-4-6/39
The Structure and Properties of Alloys in the Vanadium-Molybdenim
System
measured under a 50 kg load for 30 Bec, microhardness
under a 50 9 load.
The microstructures of the cast alloys are shown in.
Figure 2. The alloys with up to 3(ylb V are single-phased.
The alloys with 30-61Y16 V show dendritic liquation, and those
with 80-9(Ylo V have a finely dispersed precipitate with a
coarse-grained background. After the homogenising treat-
ment (Fisure,3) alloys with up to 60% V are single phased.
Alloys richer in vanadium have coagulated particles
(mainly Al 203) in the grain boundaries a nd within the
grains. Homogenisation also results in grain growth.
Addition of vanadium.to molybdenum results in an increase 3-n
hardness. The alloys havea greater hardness before the
homogenising treatment (Figure 4, Curves 1 and 2). The
2
maxiTnum.hardness is 380 kg/mm ,for the as-east allcys and
315 kg/mm~ for the homogenised alloys. Micrahardness
(Figure 4, Curve 3) is higher and the maximumlis
2
Card3/4 6?5 kg/mm, at 60--?(Ylo V. The.difference between the.hardness

SOV/24-58-4--6/39
The Structure and Properties of Alloys in the Vanadium-Molybdenu-M
System
and microhardness values is due to the preparation of the
m-Lcrosections,and the Dresence of the intergranular
constituent. The hardness-composition curve is the normal
type for metals forming up-limited solid solutions.
The plasticity deoreases with increase of the second
component (F4 gure 4, Curve 4),,, especially in the region.
2
40 - 601/o V where the tensile strength is 100 - 150 kg/mM
The greatest- plasti3ity is shown by pure molybdeiMm.
The electri---al res-Istanze-composition curve at room
temperature is shown in Figure 5. The cLrve is similar to
the hardness ourve with a maximum of 50 jig/cm at 6(Ylo V.
The results obtained corifirm,that V and Mo form a continuous
series of solid solutions.
There are 5 figure s and 7 re'Leren:.;es, 2 cf which are Soviet,
1 German and 4. English.
SUBMITTED: November 28, 1957
Card 4/4

21(l)
AUTHORS: Sergeyev, G. Ya., Titova, V. V., SOV/89-5-6-2/25

Savitaki-~-Ye. !,I., Zhullkova, A. A.,
Nikolayeva, Z. P.
TITLE: The Mechanical Properties of Uranium (Mekhanicheskiye
svoystva urana)
PERIODICAL: Atomnaya energiya, 1958, vol 5, Nr pp 618-623 (USSR)
ABSTRACT: The test apparatus (w- 41~ with which the hardness of,.,
uranium at increased tempt,.Lature and the expansion of.uranium
at increased temperature were investigated in a neutral gas
(argon), are represented by two sectional drawings. Measuring
results are given by a graph. The following details are::
mentioned:
The hardness of the uranium decreases with increasing
temperature. If temperature rises up to 6ooOC, hardness
decreases from 350 kg/mm2 to 50 k9/mm2. A regular variation
of hardness in dependence on the carbon content of the uranium
kG-07 to 0.24 16) was not observed.
The presence of carbon in uranium samples influences outflow
press-are if these samples are pressed in the at-phase. The*
Card 1/3 outflow pressure increases with an increasing carbon content

The Mechanical Properties of Uranium SOV/89-5-0-2/25
(0.09 to 0.24 %). At 6500C and a degree of deformation of
75 % the outflow pressure increases by about 6o %. For
uranium in the ~r-phaseoutflow pressure decreases from-
4 kg/mm2 at 8300C to 1.8 kg/mm2 at 10500C.
Ultimate strength and creep strength increase with an increas-
ing carbon content.in the uranium. In hot-rolled uranium with
a C-content of 0.01 ultimate strength is d b = 36 kg/mm2, in
uranium with 0.24 "' C-content = 52 kg/ . The creep
b MM2
strengths in these cases amount to 23 to 31 kg/mm2. 0 1
At temperatures of from 100 - 1500C all mechanical properties
characterizing the strengths decrease monotonously, whereas
the properties,that characterize plasticity increase. For
uranium with 0.12 ~fo C-content one finds that at 7500C
g/mm2, (3 '8 % (reiative elongation), 9# = 51 %
b = 12 k
(relative narrowing of the pressed surface), at 6oo0c
-/mm2, 23 d,,, 76 %, and at 8500C 6b
(5 b = 7 kg
0.8 kg/mm2, 6 = 31 V = 97
ff-uranium, which has a volume-centered 'lattice, has the
highest degree of pi-asticity. The.tetragonal /3-wuranium is
Card 2/3 inclined to be brittle, and velocity of deformation. ismore

129-58-8-1/16
AUTHOR: Savitskiy,_I-Ye. M., Doctor of Chemical Science, Professor,
TITLC- Physico-Chemical Properties and Fields of Application
of Rare Metals (Fiziko-khimicheskiye svoystva i oblasti
primeneniya redkikh metallov)
PERIODICAL: Metallovedeniye i Obrabotka Metallov...1958, Nr 81)
pp 2-17 (USSR),
ABSTRACT: In the first part,(pp 2-3) a generalreview is given
of the properties of rare metals 7 in the second,part
(PP 3-13) the fields of application of-the following
rare metals are discussed: beryllium, cesium and
rubidium', strontium and barium; the high melting point
metals: zirconium, hafnium, vanadium (of which the USSR
has the greatest reserves of raw materials in the rorld),
niobium, tantalumi, rhenium; the scattered rare elements:
germanium, indium, gallium, thallium, selenium
tellurium; rare earth metals (about which very'little
information is given). Most of the information contained
Card 1/2

129-58-8-1/16
Physico-Chemical Properties and Fields of Applica"tion of
Rare Ietals
in the pamper is based on publisbed non-Russian data.-
There are 22 references, 21 of which are Soviet,
1 English.
ASSOCIATION: Institut metallurGii ALI SSSR
(Institute of Metallurgy, Ac. Sc., USSR)
1. Rare earth elements--Properties 2. Rare.earth elemerts--Applications
3. Rare earth elements--USSR
Card 2/2

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21 C F-I
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of nroduction techni,:ue, o-.-"
cllemictl m~onerticri of it,~, of
"ttent-ion lirecte-' '-o t`i~-- luc` on
of rlcn -4 um ~I n(I t o '.- ii i., I o,.,.,. d 0- 0- Vl,~ im.
M.-oduct, to hie.-h costc L-.n-*- to th~ dv! --rice Of
intended luo exteml t1lic ra,.; c, n be
wed in imiustry for a number of P"Ir'041EI!, (for
r:iectric contacts, fo2- -,.n rz~~'io errio-
c ouiple 3 , Z~.--3 all ad I itu ion i.,-. t--; -e;, il ive ,.- iioy~- t~*, 02,
Other DllrDoseq). Imme(liate 7:u~t '-.,i ti':~ t
-he rhenium e d
increase 'u
to net up -I Opecinl C a 0 rr; j* fle Oil C 0 i :!::L 0 n t V: i t U e
of Mlet-liurgy i!aen-- 'T.,,7cov.
r1ard 2 12

2o-li8_4_2616i
AUTHORS: Savitskiy, Ye. M. , Tylkina, M. A. Tsygannova, I., A.
TITLE: The Recrystallization Diagram of Tantalum (n, iagramma re-.
kristallizatsii tantala)
PERIODICAL: Doklady Akademii Nauk SSSR, 1958, Vol. 118, Nr 4, PP. 720-722
(USSR
ABSTRACT: There are no data in publications on the recrystallization of
cast tantalum. In recent time, however, the smelting of tanta..;,
lum in the ard is more and more used. The highoorrosion re-
sistance of tantalum in an aggressive medium, the low fusibil-
ity and high plasticity which permits a cold working, as well
as many other properties permit to count tantalum among the
technically most important metals. The diagram in question com-
bines the grain size with the degree of deformation and the
temperature of the subsequent annealing. It is therefore es-
peciallv necessary for the metals worked by means of deform-
ation. The results obtained will make possible to choose the
deformation-,and annealing conditions in such a %Tay that the
optimum,mechaii,ical,properties of the products are guaranteed.
The authors.constructed.a. diagram of the type I for the cold
Card 1/4 working (rolling) of the cast-tantalum (figure 1). The

The Recrystallization Diagram of Tantalum 2o-118-4-26/61
conditions of cooling on a copper furnace bottom favored the
formation of a coarse-grained structure in tantalum (figure
2a). Cast bars were cold-worked by forging until rods 7 x 7-
were produced. They were annealed in vacuum at 13000 C for
two hours. Thus the coarse-crystalline structure was complet-
ely transformed in a recrystallized, fine-grained, polyhedral
structure (grain diameter 10-11k, figure 2 b). Such rods serv-
ed as initial material for the experiments. The rods were
cold-rolled without intermediate annealing, with a shrinkage
of 2,6; 5P7; 8; 10; 15; 34; 50; 68; 83; 90; 96; 98; 6%. The
rolled rods were cut into pieces of 8-10 mm. length and anneal_
ed in vacuum at 1000-25000 for one hour. The line of the
beginning of the recrystallization in dependence on.the de-
formation degree is plotted in a dotted line in figure 1. The
temperature of the beginning of the recrystallization of tanta-
lum drops.with the rising deformation'degree from 2j6 to 84%*
from 1300 to 12000 C. Vigure 3 gives some radiographs of
tantalum. The cold-rolling up t0-15% deformation.distorts the
lattice of tantalum and deforms the individual grains. The
microstructure is, however, not considerably modified. In the
case of shrinkage of more than 30~ a distinctly marked roll-
Card 2/4 ing-texture becomes visible (figure-2 v). The grains are

The Recrystallization Diagram of Tantalum 20-118-4-26/61
changed to a great extent.and extended up to....50 - 60% shrin-
kage without 6ize reduction. In the case of a deformation of
go, the grain diameter amounts to 1 - 24C. Annealing at 1000
16000 C does hot lead to-a considerable enlargement of the
grains. A recrystallization at 12000 C leads in samples with
a high deformation degree and a recrystallization at 16000 in
all samples to a complete blur of the rolling texture and to
the appearance of new fine crystallized grains of a diameter
of 6 - 13/4. The annealing at 1800 - 20000 C leads to an ab-
rupt change of size,Qf the grains in connection with.a. collect-
ing recrystallization (figure 2 g,d). The grain size increases
it 18000 C ~threefold-up to 31A and at 20000 C
tenfold (up to,115,4t). The maximum sizes-ofthe grains which
correspond to the'critical deformation degrees become visible
in the isothermal lines of annealing at laOO and 20000. In
the annealing at 25000 C an apparently specific property of
tantalum becomes visible: the size of the grainsmincreases to
an.extremely great extent-(320 - 500/#). The properties of
i
hardness and strength of.tantalum n 'individual deformation
degrees and annealing temperatures admit the assumption that
the optimum annealing treatment lies at 1300.- 1400o C. There
Card 3/4 are 3 figures and 5 references,- 1 of which is Soviet.

2o-119-2-23/6o
AUTHORS: Savitskiy, Ye. M., Tylkina, M. A., Povarova, K. B.
TITLE: Rhenium. Recrystallization Diagram (Diagramma rekristallizatsil
reniya)
PERIODICAL:, Doklady Akademii Nauk SSSR, 1958, Vol 119, lir 2,
pp 274 - 277 (USSR)
ABSTRACT: Rhenium has different mechanical and physical properties which
distinguish it from other,metals and which are also of inter-
est for modern engineering. Rhenium is a high melting 'metal,
its melting point is at 31060C. It has mechanical high strength
and plasticity properities at room temperature aswell as at
higher temperature. The following is characteristic for rhenium:
high resistance.to wear, and resistance.,against corrosion in
various a I-Oressive media. The electric resistance of rhenium
is higher than that of tungsten. Also other properties offer
wide prospects for the use of rhenium in different fields of
engineering. The recrystallization dia-ram of rhenium has
hitherto not yet.been published. The authors investigated the
Card 1/4 recrystallization diagrams of rhenium after cold deformation

Rhenium Recrystallization Diagram .2o-119.-2-23/6o
(rolling) of cast and metal-powder camples. An initial material
served the powder of meLallic rhenium which had been reduced
from potassium perenate (perenat kallya).Prdtathis powder the
samples were produced by powder metallurE;ical methods. These
rhenium bars were melted in an arc furnace in an argon atmosphe-
re at a pressure of 200 torr. The coarse crystalline structure
of the cast metal could beremoved. The samples had a re-
crystallized polyhedral structure with a L=ain diameter of 40[L
and served as initial material for the wholeviork. The treat-
ment of the samples is shortly discussed. The temperature at
the beginning of recrystallization was determined by means of
X-ray methods from -thc occurence Z)f the first points on the
diffraction rings. A diaL:ran shows the temperature of thebegin-
ning of recrystallization of rhenium as a function of the de-
gree of cold deformation. This temperature drops with increasing,
.deformation degree 17500C at %fadeformation to 12000C at
4o -6o,fo deformation. In cold deformation of rhenium the grains
were crushed. In the case of low compression degrees the forma-
tion. of deformation twins is observed.in rhenium..Further de-
Card 2/4 tails are discussed. The Itemperature of thle beginning of re--

Rhenium Recrystallization Diagram 2o-1,19-2-23/6o
crystallization of powder metallurgical rhenium drops with
0 0
increasing deformation do'~ree from 1850 C at 5 % to 11:00 C
'j
at 48% of deformation. A diagram shows the dependence of
the size of the grains on the temperature of annealing as
well as on the degree of deformation. The temperature of
the beginning of crystallization of molten rheniu,-.i is lower
than that of the beginning of recrystallization. of powder
-metallurgical rhenium which is explained by the.different
degree of purity of the material as well as by the presence
of a microporosity in powde3~metallurgical rhenium. According
to the data on the recrystallization and on the.change of
the hardness of rhenium the optimum temperature for annealing
of.the~rhenium deformed with a compression degree of more
than 10% the temperature range from 1750 - 24000C can be
assumed. There are 4 figures and 7 references, 5 of which
are Soviet.
Card 3/4

Rhenium Recrystallization Diagram 2o-110-2-23/6o