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

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001447410019-0
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: March 14, 2001
• Sequence Number: 19
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

PUSE .1 BOOK EXPLOITATION SOV/4654
Savitskiy, Yevgeniy Mlikhaylovich, Professor, Doctor of Chemical Sciences
Redkiye metally i splavy (Rare Metals and Alloys) Moscow, Dom tekhniki, 1959.,
83 p. No. of copies printed not given.
General Ed.: I.I. Novikov, Candidate of Technical Sciences, Ed.: V.V. Pereverzev;
Tech. Ed.: V.I. Zykin.
PURPOSEa This book is intended for workers of scientific research institutes,
design bureaus, and various plants.
COVERAGE: The book presents the latest information onthe structure,.use, and
properties of rare metals and metal alloys' containing rare elements. The
first and fourth parts of the book review the principal physicochemical
properties of rare elements and present data from published works concerning
the industrial use of these elements mainly in various constructions and
instruments. The second and third parts of the work discuss- the results
of efforts of the author and his coworkers to determine certain properties
of rare metals and their alloys and to construct equilibrium diagrams for
systems containing rare elements. VS. Baron, V.F. Terekhova) and M.A. Tyl-

Rare Metals and Alloys SOV/4654
kina, Candidates of Technical Sciencesjdirected laborator experiments
conducted in the Institut Metallurgii Akademii Nauk SSSR finstitute of
Mletallurgy, Academy of Sciences USSR]. There are 21 references: 16 Soviet
and 5 translationstto Russian)
TABLE OF CONTENTS:
Principal Physicoehemical Properties of Rare Elements 5
Light-weight rare metals 6
Refractory metals 6
Scattered rare metals 7
Rare earth metals (lanthanites) 9
Radioactive rare metals
investigation of Mechanical Properties and of Recrystallization Processes
in Rare Metals and Alloys 18
Ductility of polymorpho.us metals .20
Influence of temperature on the ductility of germanium and silicon 23
Properties of metallic compounds 26
Card-~/.-3-

l8(4,?);25(l) PHASE I BOOK EXPLOITATION SOV/2568
Akademiya n'auk SSSR. Institut nauchno-tekhnicheskoy informatsii
Metallurgiya i metallovedeniye; khimiya, metallovedeniye I obrabotka
titana (Metallurgy and Metallography; Chemistry, Metallography,
and Treatment,of Titanium) Moscow, Izd,vo AN SSSR, 1959- 383 P.
(Series: Itogi nauki; tekhnicheskiye nauki, 2) Errata slip in-
serted. 2,700 copies printed.
Ed~: N~ V. Ageyev, Corresponding Member, Academy of Sciences, USSR?
Yu. V. Rylina.
Eei-of Publishing House: V. S. Rzheznikov; Tech. Ed..
PURPOSE: This collection of articles is intended for metallurgists
working .,rith,titanium and titanium alloys.
COVERAGE: The articles in this collection deal with the chemistry,
metallurgy, and machining of titanium and titanium alloys. The.
articles are based on abstracts appearing in the Referativnyy
zhurnaly for chemistry and metallurgyjfrom 1953 to 1955. For the
most part the articles are based on non-Soviet-material. No person-
alities are mentioned. References follow each articlea-
Card 1/6

Metallurgy and Metallography; (Cont.) SOV/2568
TABLE OF CONTENTS:
1 nd Titanium Alloys
Ageyev, N. V. Crystal Chemistry of Titanium a
and Campounds
This is a review of.studies in the crystallography of metallic
titanium and a number of its compounds. Intermetallic compounds
covered are those of titanium with metals of Groups I, III, V,
VI, and VII. Data on compounds of titanium with nonmetals and
metalloids of Groups III, IV, V,.VI, and.VII are also presented.
Kornilov, I. I., and P. B. Budberg. Con*stitution Diagrams of
Titanium-base Systems 31
Binary and ternary titanium-base systems are studied. It is
~sho,wn that in binary systems,'the nature of the chemical reaction
between titanium and the given element is determined by the
position of that element in the periodic table. Formation or non-
formation of a solid solution is dependent on the*degree of simi-
larity between the two elements. Data on the solubility ofl.vari-
ous chemical elements in titanium are given in a number of tables,
Card 2/6

Metallurgy and Metallography; (Cont.) SOV/2568
arranged according to chemical groups. A set of 18 constitution
diagrams of ternary titanium-alloy systems is Included. It is
stated that these diagrams represent virtually all known data on
these systems published up to 1955.
Savitskiv Ye M.,and M. A. Tylkina. Properties of Titanium and
'_T~ianjum Alloys 103
This is a survey of the physical and mec-hanical properties of
t!"anium and titanium alloys. Data are given on the effect of
o- .-3n, nitrogen, hydrogen, and carbon on the mechanical prop-
erties of titanium.
Gudtsov, N. T., and L. D. Mashtakova. Heat Treatment of Titanium
an&Titanium Alloys 163
The authors discuss work hardening, annealing, grain refining,
and other heat-treating methods for titanium and titanium alloys.
Also discussed are the effect of alloying elements on heat--
treating characteristics, mechanical properties after heat
treating, and structural changes at heat treating.
Card 3/ 6

M6tallurgy and. Metallography; (Cont. SOV/2568
Arzhanyy, P. Thermochemical Treatment /Diffusion Coating/ of
Titanium, 187
This article deals viith the nitriding, boronizing, and sili-
conizing of titanium.
Shelest, A. Ye., A. N. Danillchenko, and I. M. Pavlov. Forming
of Titanium and Titanium Alloys 195
The authors discuss the special features of plastic deform-
ation, general characteristics of cold and hot working, in-
dividual forming operations, preparatory and finishing oper-
ations, organization of production, and storage ani,utilization
of waste.
Savitskiy, Ye. M., and M. A. Tylkina. Recrystallization of
.Titanium Alloys 226
Recrystallization of magnesium-reduced and iodide titanium is
discussed in reference to its occurrence after cold working,
hot foIrging, annealing, tempering, and hardening. Data are also
Card 4/ 6

18(7) PUSE I BOOK EXPL41TATION SOV/3355
Akademlys nsuk SSSR- institut metallurgil. Nauchnyy.aovet PC
probl4m* zharoprochnykh aplavov
lealedovanlya PC zharoprochnys splavam, t. IV (Studies on Heat-r,-
400
N SSER
19
9
.
p.
5
,
distant A.1 01", '01 4) Moscow, Izd-vo A
t& i.200 copies printed.
"
Al
Z
,dh,,, House.. V, A. r Klimov; Tech. Ed. iA. P. Guneva;
1,ub
:r
d
.
torial -Board : 1. F. Bardin, Acadeciteian; 0. V. Kurdyumov,
Edl
.
Academician; M. V. Ageyev; Corresponding Member, USSR Academy 0

3ci*ncea, MPavlov, and 1. F. ZudIn, Candidate
- 1. A. Oding, 1..
or Technical Sciences.
PURPOSIs This book Is Intended for metallurg-Isto concerned with
the structural metallUrgl Of alloys,
CQVZRAGRi This to a collection of special'.Z*d studied Of varloUs
l
oys.
robleol In the structura I metallurgy of host-rdalstant al
-
l
d

,33
en, 00.0 with
.. r. with theoretical princip
-
3
es
criptions of now equipment and methods, Others vItn propert
VarIoua. phenomens, occurring under
0 =tr=-1
;'.c'fI4d conditions atudlad and reported On. For details,
%r
as Table of Contents. The articles are accoa,pa;!44 by a num-
:
-bar. of-raferances. both Soviet and ooa-3071.st.
Studies (cont.) 30v/~3
55
99;TAYI.T. A- P. , and 1. V Chernsnlk~o Iffect or Plastic,
'
'
D*fOrmtl*n 8M Lo.
T
$a
ar tures
on
ths
HelLt~ es1stant
_
Fr _g
OP*rtie& Or Type 18 TT A., ni Lc %s.1
t
c
.
214
~
Rociyatallization or
'N
v4k
'i~
.
.
TIt&njum,-HirnIump Tantalum, Rhenjum
ta :
.
And Tungsten. And Th, r Alloys
,

1B
(Irldnev v x - V I Trert;ioy. and A. 9. Erf* ct

~-
"
;
---'of I ct*u
Z
* Q
?iidtlcltY of Chroilkog 226
Aasysv.
I V- and V ':";nznikOv
Production or Pure
R
Chr4
.
~ 237
Svechnilcov
V_X.j Kocher.-hlz*Xly, V. M ran,-
-
--ye--ye
.
and A -Shur.1n, A
udY of the
a ~yX.~ ~
nadjum
st
em
y
248
Grua Grzh Imm.)r-u - X.--V-. 1
and-D-1-2,roko:tyvv~ Constitution
la'rael of the Ternary System 0tromiuli-Tungsten-MolybdanLIX 257
Card 8/12

ob
all
oil A.
fit 1 A
Iva
64 a Will
OV 4
fit a
1,14 IV I. I

VOL, Abram Yevgenlyevich; AGRYBVI N.Y., red.; ABRIKOSOV, H.Kh., doktor
takhn.nauk, red.; KORNILOV, I.I., red.; ;jAYTIP'.CWTY, Ys-X,, red.;
OSIPOV, K.A., doktor tekhn.nauk, red.; GUSZVA, L.N., kand.khis.
nauk. red.; KIRGALOYMAYA, M.S., kand.khim.nauk, red.; SMMOV-
SUTA, I.Tu.. red.; MURASdOVA, N.Ta., tekhn.red.
[structure and properties of binary metal systems] Stroenie i svoistva
dvoinykh metallicheskikh sistem. Pod rukovodatvom H.V.Ageeva. Moskva,
Gos.izd-vo fiziko-matem.lit-ry. Vol.l. (Physicochemical p*roperties of
elements; nitrogen, actinium, aluminum, americium, barium. beryllium,
and boron systems] Fiziko-khimichaskie avoistva elementov; Sistemy
azota, aktiniia, pliuminiia, ameritsiia, bariia, berilliis bore. 1959.
755 P. (Mi;; 13:3)
1. Chlen-korrespondent AN 3&9R (for Ageyev).
(metals) (Phase rule and ~4uilibrium)

SAVITSM, Ye. M.
"Influence of Tempezature on Mechanical Properties of Intermetallic Compounds."
paper presented at the Electrochemical Society Meeting in Philadelphia, 3-7 May 1959
Eval. B-3,131,2o4

_9,113~',71"6010()()I()Cglol8l"rj2g
A006/AO01
Translation from: Referativnyy zh-urnal, Metallurgllya, 1960, No. 9, pp. 257-25:3,
21596
"I
AUTHORS~ Savitskly, Ya,M..'.Terekhova, V.F., TS!kalov, V.A.
T 1, Ma Investigation of the Physi- Ch-mical Enteracticne of Rare._Ear-,.h
Me~~als With 1rsn and Steel
'RIODTCAL. '%eik
_P V sb,: ozelme"n. elementy.v =taiyakh i splavakh, Mosoow,,
P
Metallurgizda-,, 1959, pp. 31-49
T.M. - Tbe,authors studied 'he interaction of rar _e
e arth metalz~, su^h as
La an P, W 1-th 3, 0, S1 and C of stee'L and ths effect of Ce and La cn the mechaxn-
10al DrOpertiSS Of Fe. `1ne Fe-La syztzam, with up 2 we-Ight percent I-,-, was
studied by microscopical, e1ectronosr_-:pa_-;al and mechanical methods. 141- is =_St~cc_
113hed that small additions Pf'rare-earth metals (0.2-0.5%) refine --P.-S.-Iderably
the structure of Fe and steel. Rare-earth metals are strong deoxidizers wh!_,h
cau-se 'the fine-dispersed distribut.lor. of cKide imp-,rit-lez, The addit~.,-n of 0.2-
re-earth.metals to steel containlLng -~O.1% cause c)n=ldera'-Ie de~-jllfur!-
0,5% ra
Card 1/2.

3/1 1/6 CO/009/0 1,/
-3 O/C
A006/AO01
of Rare_-Earth Metal's With ir-
Investigation of the Physico-Chemical L -.n
and Steel
za-,,_c~, , At a S content of 0.02-0.0y%, ot s ri e i Ph6
preczance of < 0.2% Si In "he st~eel does not r&-J,_:,-e the relrlnlng e f f e- c ~, _- fGe.
ced into the In a, i r t e r aa: t
The rare-earth me-als introdu a~nount of 0.9-1.c
-!,he cerlit,e z~t-_ntent in _ e
with C, forming carbides, and redu-,e considerably
The addition of 0,1-0,2~6 rare-ear-h m~_-a:iz causes strength" du---
tility and ak of steel. An increase of the ra:re-earth metal 1~,:,nteni% from 0 t
373%'reduce-z the mechani-cal propertle!i of Fe Lrd sll~_el du-, to the fo_rmP.:t!.-,r1 :f
brit'sle intermetallic compounds of Fe with 1.-,he rare_earth.m=_,~als, At a D-3 C-:m-
tent of 7 0.4-0.5 weight %, a second phase !.z- o"c-served.-in the Fe-La system.
Solubil-l-w of La in ~ -Fe is greater than In Cv -Fe. A conSiderable imurovemen-.
of physicc-mechanical properties cf Fe_A1)L11CYs wa_~ cbservEj -.-then rare-earth
metals were intr-Dduced in an amaun~. of up 5 wr-lght
A,R~
T7ra_n1'3Iat-o_- s note: This tte full i3f -,t~ T-_,glmal Ru s s1 a n ah I r a
~Gard 2/2

BOV/136-59-1-12-/24
AUTHORS: Savitskiy Ye M and-Terekhova, V.F.
,TITLE: Yttrium and its.Alloys Mtriy iYego splavy)
PERIODICAL: Tsvetnyye Metally, 1959, Nr 1, pp 48-53 (USSR)
ABSTRACT: The authors have carried out an investigation of the
microstructure and properties of yttrium and its alloys
and the reaction and in4uence of the element on alloy
properties. Yttrium foei-the in*vstigation was supplied
by D.D. Sokolov2 L.A.Izhvanov and N.P.Vershinin. The
Purity of the metal was 96.5%, its microstructure
characterised by inclusions of a second phase bofh- at
grain boundaries and within grains (Fig 1). The Brinel
hardness was 80-85 kg/mmP- and the ultimate strengths In
tension and compression were 16 and 82 kg/mm?-., It was
found'that yttrium is completely dissolved by cqrium;
with aluminium, iron and copper eutectic mixtures are
foundi in alloys with chromium,,titanjum and zirconiumg
yttrium. does not dissolve in large quantities, with
peritectoid reactions over small concentration ranges and
immiscibility in the solid state at higher yttrium
Card 1/3 contents; yttrium-is.practically immiscible,w$th
vanadium, niobium~ tantalum and molybdenum. The

S
Yttrium. and its Alloys OV/136-59 1-12/24
introduction of 0.1 0.2% yttrium refines the grains of
almost all the --ast metals studied, but with aluminium
and magnesium the opposite effect is produced. Yttrium
has a deoxidizing and inoculating affect on all the,
alloys and with magnesium and aluminium. the element has
a hardening effect. The authors recommend that the study
of the alloying action of yttrium. should be made the
Subject of special investigations.
Figs 3,1+,6 and 7 show micrositructures of alloys of
yttrium with aluminium ' chromium, copper and zirconium)
respectively, Fig 2 shows the macro- (left) and micro-
structures (centre and right) for a 10-% Y magnesium
alloy,and Fig. 5 the microstructures of-10-% Y alloys
Card 2/3 with molybdenum (left), tantalum (centre) and vanadium

dw
SOV/129-59-3-9/16
AUTHORS. Savitskly, Ye.M., Terekhova, V.F. and Burov, I,V.
TITLE-~ Influencae of Riie Metals on the Mechanical Properties
of I-ron-aluminium. Alloys (Vliyaniye redkikh metallov
na mekhanicheskiye svoyst-va zhelezoalyuminiyevykh
zplavov)
PERIODICAL: Metallovedeniye i Termicheskaja Obrabotka Metallov,
19q
pp 38 - 43 + 2 plates (USSR)
Nr 3
9
,
,
ABSTRACT: Up to relatively recently, it was not possible,to
produ,~-.e Fe-Al alloys with alLuninium. content of about
16 wt.% with an elongation at room temperature
exceeding The cause of such.brittleness was
obvLously the large quantity of non-metallic Al 2 03
inclusions, the presence of a considerable quantity of
admixtures in the original iron and also the formation
of chemical compounds and ofsuperstructures.~ The
increase Id brittleness is also brought about by the
tendency of these alloys to form a large number of micro-
cracks due to low-temperature conductivity and also due
to the tendency to grain growth. The authors investigated
Cardl/5 the effects of applying rare metals for improving the

SOV/129-59-3-9/16
influen--e of Rare Metals on the Mechanical Properties of.
iron-a-luminium Alloys
mechanical properties of alloys of this type. The
alloys were produced using as starting materials
electrolytic iron of 99-58%o purity and aluminium of
99.9% purity. The influence was investigated of alloying
additions of the following elements: Zr, Ti, Ta, Nb, VS
B- Mo, Ce.. The additions,were selected for ihe purpose
o~ determining their influence,as deoxidation agents,
inoculation substances and carbide-forming substances
The chemical composition of the investigated 38 alloy;
is entered in Table 1, p 40. The effect of the individual
elements on the mechanical properties was investigated
and also on the magnetic and the technological properties.
Jn Figure 6,.the dependence of the hardness on addition-s-
of raxe metals is graphed for iron-aluminium alloys
~;ontaining 15-1&116 A!. In Figure ?, the influence of
cerium on the macro- and microhardness of iron-aluminium
allo,ys is graphed.. In Figure 8, the influence of
additions of rare metals on the strength of iron-alumanum,
alloys is graphed. Figures 2-5 show microphotos
Card2/c

SOV/129-59--3--9/16
Influen~_-e of Rare Metals on the Mechanical.Properties of
Iron-aluminium alloys
(magnification 100 times) of Fe-Al alloys containing
various additions and also non-metallic inclusions.
In Figure 9, the influence of *zirconium and tantalum
on the durtility of Fe-Al alloys during Ihot rolling is
graphed, Rumerical data on the influence of zirconium
and -tantalum on the impact.strength of alloys are
entered in:Table 2; numerical data on the influence,
of Ta, I Zr and Ce on the tensile strength o'L'-Fe-.Al alloys
axe en'tered.in Table 3. The authors arrived at the
following oonclusions.l)The main harmful admi-xture which
which f ormz-
.~ausas brittleness of Fe-Al alloys is oxygen,
c--~clusions of aluminiu-M oxides along the boundaries,and
'ing
in the body of the grains. A good method of produ,;_
alloys with a minimum content of oxygen is induction,
Sme]-ting, in a pure helium atmosphere,,in crucibles made
of aluminium. oxide and introducing aluminilim on the
surfa,-,e of themetal. It is necessary to deoxidise
primarilythe iron in vacuum with carbon,or hydrogen..
'Card3/"-- 2*' An appresiable refining of the grain of Fe-Al alloys

SOV/129-59-3-9/16
Influence of Rare Metals on the Mechanical Properties of,
Iron-aluminitim Alloys
occurs as a result of additions of Ti and combined
additions of cerium with zirconium, cerium with
molybdenum and cerium with vanadium.
3) Boron and vanadium,in quantities up to 0.05 - 0.2016
increases appreciably the hardness of the alloys.
The st-rangth of the alloys increases from
2
22 - 39 kg/mm as,a result of addition of O.Oylo boron;
tantalum (0.2%) and zirconium (0.5916) increases the
strength by 20 - 25 kg/mm.2 and also the impact strength
and the ductility d-aring hot rolling.
4) Magnetic Fe-Al alloys can be easily deformed in the
hot state and rolled into.sheet Non-magnetic alloys
(based on FeAl compounds) can be rolled only if the
op'imum ollin regimes are equally complied with (a
r I
9
we!"-,--t:::-ea"Ied surface, small values of reduction, low
speeds of deformation and strict adherence to the specified
temperature conditions).
Card4/5 Combined alloying with cerj-um (0.2 vanadium (0.25%)

SOV/129-59-3-9/16
influence of Rare-Metals on the Mechanical Properties of
iron-alumini,am A.110,7S
and mrlybdenilm (1.8%) brings about a shift in the line of
'he magn_=t..-La transformation of the iron-aluminium alloys
(f--r-:m 1-6 'to 1-Wo Al content).
61, Ntz~pe of the investigated alloys oxidises in air at.
2C0 ,C and all have a :corrosion resistance Icommensurate
wL ~ha-t c-" refzactory steels L
t The specific gravity of
sush F=-All alloys (containing 16% Al) is 20016 lower than
the specif'ic, gravity of steel.
-7) U
Ii-on-al:uminium alloys alloyed with small quantities
of ceri=., !.zixconiuml, tantalum, etc. -.:~an be applied as
~elativalv --heap h-igh-strength materials at room and at
ele7ated temperatures and also as materials with a high
cesistance to corrosion. There are 9 figures, 3 tables
and 15 references, 5 of which are Soviet, 1 Japanese,
1 German and 8 English.
ASSOCIATION: Institut metallurgii AN SSSR (Institute of
Metallurgy of the Ac.Sc.USSR)
Card 5/5

AUTHORS: Savitskiy, Ye.M., Tylkina, M.A. and Shishkina, L.L.
'-( ~os c 0~w
TITLE: The Phase Diagram of the Tungsten-Rhenium System and
Properties of its Alloys
PERIODICAL: Izvestiya Akademii.nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1959, Nr 3v PP 99-107(USSR)
ABSTRACT; Microstructural and X-ray investigations were used as
a basis for constructing the phase diagram. -Melting
points, hardness and microhardness of the various
constituents were measured. The resulting phase
diagi-am.is given in Fig 1. Microstructures are shown
in Fig 2 and 5 and X-ray photographs in Fig 4. There is
a solid solution (a) up to 45%.Re near the alloy melting
pointu falling to 32110 at 1100 C. In this region
hardness increases Iwith increasing Re content to.420.kg/
mM2 at 25,-o' Re., Aperitectic reaction takes place at,
2890aC. Liquid +aita. The a phase has a complex tetra-...
gnal lattice with a =-9.53A, c =-,,4k.95A and c/a = 0.52.
This phase extends from 40 to 66 wt % Re at 11 00aC and
from 45 to 66% at 20000C. It is very brittle and has a
hardness of 2000 kg/mm2., The solid solution of tungsten
Card 1/3 in rhenium extends to 14,0% W near the melting point and

sov/180-59-31-17/43
The Phase Diagram of the.Tungsten-RheniumSystem and Properties of
,its Alloys
12% at 11000C. There Is A eutectic between the a phase
aInd the P solid solution at 75% Re and 2815%. The
microhardness of,the eutectic is 800 kg/mm4. The two
phase region (P + c) is very 'narrow. There. -is a
peritectoid reaction as follows: a + Pq=*X. The X phase
has parameter a = 9.57A and is of the (x-Mn type. Its
microhardness is 1500 kg/mm2. Alloys with up to 20% Re
have high electrical resistance, strength and plasticity.
Fig 1 shows the influence of temperature on pro'erties
p
and Fig 5 the influence of Re on strength. W-Re alloys
could be used in the electrical industry. Fig 6 shows
the external -appearance of electrical contacts after
corrosion in moisture. Re after 50 days (a) is-in much
better condition than W after 30 days and (b) W-Re alloys
could,also be used in industry where high mechanical
properties and close tolerances are required. There are
Card 2/3 6 figures, I table and 11 references, 3,of which are

18(6)
AUTHORS;
TITLE:
PERIODICAL:
ABSTRACT:
/78-4-2-27/40
SOV
SavitsklY, Ye. M.~ Tylkina, M. A., Povarova? K9 Bo
The Phase Diagram of the System Rhenium-Molybdenum
(Diagramm-a sostoyaniya sistemy reniy-molibden)
Zhurnal neorganiohesVoy khimili '1959; Vol 4, Hr 2,
PP 424-434 (USSR)
The phase diagram of the system Mo-Re was drawn on the basis
of the results obtained by physico-chemical and analytical
investigations (determination-of the melting point, mi-.--ro--
scopic, X-ray, and phase analysesq determinations of the
speei fic'electric resistance, and detle,rmination of solidity).
.For the produotion of the alloys max-Imum purity rhenium
(99.8%),and molybdenum,(99.6%) were used as initi Ial mate_~_ials.
The pressed samples weresintered in vacuum at.15000- In the
system rhenium-molybdenum solid solutions containing 58 weight%
rhenium'(42 at % Re) are formed at temperatures near the
..melting.point. The solidity of molybdenum alloys increases,
in the field of solid solutions, from 130 kg/mm2 (pure
molybdenum) to 205 kg/mm2 for -the alloy containing 53'weight7'af
rhenium. In alloys with 43-46 weight % rhenium the liquidus
Card 1/3 and solidus curve of the solid solutions.show a minimum at'a

SOV/76-4-2-27/4 0
TI-,.e Phase Diagram of the System Rhenium-Moly1cdenum
temperature from 2450�30'. The X-ray analysis showed that
upon increase of rhenium content the lattice constant in the
solid solution is reduced and is 3.12 X in the alloy with
53 weigh-,,- %. The determination of the electric.resistance con-
firmed the range of solid solutions. The specific electric
resistance of pure molybdenum is 6i.6.10-6 ohm-cm, and rises
to 27.6.10-6 ohm-cm i,n alloys with,42 weight %Irhenium. In Ithe
system Mo-Re the I-phase (Re Ito ) is formed after a peritea,tic
5 2
reaction at 25700. The lattice parameters of the a-phase are:
a = 9.54 1 and C = 4-95 X. The micro-solidity of the 6-phase
is 1850 kg/mm2 . The specific electric resistance of the a-
phase is stronger than that of the solid solution and amounts.
-4
3.1.10 ohm-cm in the alloy with 78 weight % Re. The dl,-
phase field a + a exists between the 6-phase and the field
of solid solutions. The morio-phase field of solid solutions
of molybdenum in rhenium exists.at the melting point tempera-
ture starting,w,th 10 weigh. % molybdenum and amounts up to
Card 2/3 2-3 weight 34 Mo at 1100 0. The solidity of the alloy with
----------

SOV/78-4-21-21 '40
The Phase Diagram of the System Rhenium-Molybdenum
2 f 2
95 weight % Re is redu!,-ed to 320 kg mm and to 290 kg/mm in
pure rhenium. In zhese alloys all'so the electric,xes-istance
is reduced to 5T-10_0 ahm.cm for "he alloy with 95 weight % Re.
In the system Ito-Re 'the phase -Y_ is formed after the peritectic
at 18500. The peritectic change a + takes
place in alloys Iwhich contain 81-95 weight % rhenium. The
phase.has the structure of typea-Mn as has been found by
X-ray analysis. The microscopir,~ examinations of so-Lidity and
electrip, resistance of allcys with 81-95 weight,% rhenium
prove the existence of the X -phase. The solidity and electric
resistance of the alloys are increased by the formation of the
new phase X . There are 7 figures, 2 tables, and 11 references,
3 of which are Soviet.
ASSOCIATION:, Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov of the Academy of
Sciences, USSR)
SUBMITTED: November 25~ 1957
Card 3/3

18(6) SOV/78-4-2-28/40
A.UTHORS: Terekhova, V. F., Kholopov, A. V.
TITLE: The Phase Diagram of the Alloys of the System Chnomium-Cerium
(Diagramma sostoyaniya splavov sistemy khrom-tseriy)
PERIODICAL- Zhurnal neorganicheskoy khimii, 1959, Vol 4, Nr 2,
pp 435-438,,(USSR)
ABSTRACT: The phase diagram.of the alloys chromium-cerium,(up to,
30 weight ~ cerium) was investigated by micro-structure analy-
ses, thermal analyses) and X-ray analyses. Electrolytic
chromium (99-5%) and metallic cerium (99%) were used-as
initial materials. In the system chromium-cerium separation
into two layers takes~place i-n a wide,range (10 to 50% cerium)
upon liquid-state at 17600o The analyses of the micro-structure
of the alloys show that in the field of the solid solution
the s -olidity of the alloy rises upon increase of cerium
conteht. Cerium additions amounting from 1-1-5% to chromium
increase the solidity of chromium and refine its structure.
Alloys ofihe system ohromium-cerium with cerium contents
3% are unstable In air and decompose while cerium oxides
Card 1/2 are formed. The liquidus and solidus curves of these alloys

SOV/78-4-2-28/40
The Phase Diagram of the Alloys of the System Chromium-Cerium
were determined. D. Ya.,Svet,and V. V. Grishin participated
in.these determinations. The solubility of cerium in solid
chromium,was.determi-ned and it was found that the solubility
is 2-3% at.15000, 3-5% at 16000, and 5~10% at 17000. The
solubility eux-re of cerium in solid chromium2 depending on
the -temperature, was.drawn on the basis of the micro-structlire
analysis* The phase diagram of the alloys chromium-cerium
(up to 30% cerium) was drawn according to data on micro-
structure and thermal analyses. There are 8 figures, 2 tablesv,
and 7 references, 4 of which are Soviet.
ASSOCIATION: Institut metalluigii im. A. A. Baykava Akademli nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov of the Academy
of Sciences, USSR)
SUBMITTEIY: November 29, 1957
Card 2/2

118(6),18(7)
AUTHORS:
TITLE:
P-11IODICAL:
ABS'TRACT:
Savitskiy, -ie. M., Tylkina, LT. A., SOV/78-4-3-34/34
flotlyev, Yu. A.'
The, Phase Diagram Rhenium - Titanium
(Diagramma sostoyaniya sistemy reniy-titan)
Zhurnal neorganiche3koy khimii, 1950P,Vol 49 Ur 31 pp 702-704
(USSR)
The system rhenium - titaniun .-,as inve:3tigatcd by the method
of metallographical analysis and "-"-ray analysis. Melting point,
electric resistance and hardness of the alloys Ivere determinedo
As initial materials titanium and rhonitm with a. purity of 99.6%
were used. On the basis of investi-ations,an. orientation phase
diagram of the system ~.,.as plotted. In the system solid solutions
of rhenium occur in P titanium which spread upto 80 vit%
rhenium. At -95 wtc/frheniiim(82-5 a tt'oM"::;) tbe cherical compound
Re Ti is formed. This compound is brittle and the hardness
24 5 2. The solubilit-r of titanium in
amounts to.1800-2000 kgp/mm
rhenium amounts to sev
oral By means of mic-rczcopic and
X-ray analysis and the dilat.ometric invevti--ation of the alloys
rich in titanium the limit of the Phase ran~-'Cs c.L 0C+ and

The Phase Diarrram Phenium 44
was fixed. The solubility o f r1h e ni i n ce- to i t a n _J u= am o un t s
0 * derably wi U~
at 7250 to -1~~ and rises inconsi 1 11
temperature . In alloys .-dith 10-1571' rhenium th~e a; phase -;ccursF
which was also confirmed by X-ray analysis. The det e rini nations
of the electric resistance of the alloys hard!~ncd at -.rarious
temperatures show that with an increase of therhenium content
also the electric resistance increases. The electric resistance
in alloys hardened at 7000 with 23.7; lie amounts to
1311A. ohm-cm and in the case of alloys with purest titanium
to 44-5/14. ohm-cm. Alloys r:ith 46c% rhenium shoy. -no noticeable
increase in the electric resistance. The alloys hardened at
900o have -- hiolier electric resistance than those hardened
at 7000. There are 2 fi8-ures and references, 2 of which are
Soviet.
ASSOCIATION: Institut metallurgii im. A. A. Daykova Alkadem-ii nauk.SSSR
(institute of Metallurgy imeni A. A. Baykov of the Academy of
Sciences, USSR)
SUBIMITTED: April 2, 1958
USCGE-DC-60,727
Card 2/2

18(6) SOV/78-4-6-43/44
AUTHORS: Savitskiy, Ye. bl., Terekhova, V. F., Tsikalov, V. A.
TITLE: The Phase Diagram of the Alloys Aluminum-Yttrium (Diagramma
sostoyaniya splavov alyuminiya s ittriyem)
PERIODICAL: Zhurnal neorganicheskoy khimii, 1959, Vol 4, Nr 6,
PP 1461 - 1462 (USSR)
ABSTRACT: The system aluminu---yttrium was investigated for the first
time. Alloys.up to 60 percentages by weight yttrium were
produced and investigated by metallographic, thermal, and
X-ray stractural,analyses and the microbardness -;as.determined.
Aluminum of the type AV-000 and metallic yttrium of a purity
of 99.6% were used as.initial materials. The phase diagram
of the alloys aluminum-yttrium (60,percentages by weight
yttrium) is a complicated system with occurrence of chemical
compounds (Fig 1). Chemical compounds occur as crystals in
alloys with 13.5 and 42 perceitages by weight yttrium. The,
Cj
microstructure of the alloys aluminum-yttrium with 0.34,
8-78. 42.1 and 57.) percentages by weight yttrium is given
Card 1/2 in figure 2. Alloys with 57.3 percentages by weight yttrium

The Phase Diagram of the Alloys Aluminum-rttrium SOV/78-4-6-43/44
have a composition which corresponds to the formula Al 512'
The microhardn,ess of this alloy amounts to 600 kg/mm2. By
the X-ray struc tural analysis it was found that this compound
has a complicated crystal structure. Further investigations
are necessary for the completion of the phase diagram aluminum-
yttrium. There are 2 figures.
SUBMITTED: January 30P 1959
Card 2/2

18(6) SOV/78-4-6-44/44
&UTHORS: Savitskiy, Ye. M., Terekhova, V. F., Burov, I. V.
TITLE: Investigations of the Alloys of Niobimm With Lanthanum and
Cerium (II s2ledovaniye splavov niobiya s lantanom i tseriyem)
PERIODICAL:, Zhurnal neorganicheskoy khim-ii, 1959, Vol 4, Nr 6,
PP 1462 1463 (USSR)
ABSTRACT: Thermal-i microstructure-, and X-ray analyses were carried
out in the alloys of niobium with lanthan
um and the hardness
and the electric resistance were determined. On the strength
of the investigations phasediagrams of the'systems niobium,
cerium and niobium-lanthanum~(UP to.50 percentages by weight
cerium and.lanthanum) were constructed and given in figures
1 and 2. Niobium of a purity of 99%, metallic.lanthanum of 99%,
and cerium of a purity of 98.9% were used as initial materials.
It was found that.niob.ium Tith lanthanum and cerium has in the
liquid and solid phase wider immiscible regions.,The formation
of layers in the system nioblum-cerium begins already in the
case of 1 - 2~1- cerium and in the alloys niobium-lanthanum in
Card 1/2 the case of 0.1 0.2% lanthanum. The solubility of cerium

R(2)
.1 .90V/78-4-!-8-37/43
AUTHORS: Savitskiy, Ye. M., Tylkina, M. A., Povazovap.K. B.
TITLE: The Phase Diagram ..,of- the, Sys tam Chromium Rhanium (Diagramma
soatoyan,iya-sistemy.khr-om zaniy)
PERIODICAL: Zhurnal.~neorganichaskoy,khim:Li, 1959,-Vol.4, Nr 8,
pp 1928-.--19-30 (TJSSR)
ABSTRACT: By.meana of variaus phy-slaoionchemical-matbod-a (determination of
the melting point.,,-micrai3copia-.analvais, . X%rzy ana4ais,
meaauremeats.. of. harAneAs..ajid. miaroha_7-_dnajLs), the . phase- diagram
chroaLiums--rheni-rn.-.was.-de.texminjed.. (Fig....1.) ..-Some- microstructures
of.-cast-or thermally proceased~alloys_are.shown in figure 2.
.The ph&se__-d�&graaz,3how_s. a;.peri_tectic_ type. The per-itectics
are -between. U,509,~ (-1.iqu1d...pha",,+_ P and-.2280' (liquicl
phase + data (the solid a-solution is formed on Cr- asi
b s, the
solid sol:ution*on' Rh.:basi'h)). The hardn~ 8s of'the s6lid solution

rhen um- "con-itehi-t~'(138 1k1mm
increases with the 2-for pure-Or,
2-
322 kg/mm. for the alloy with 63-5 % by weight Rh). The one-
phase range ofthe solid solution of chromium and rhenium was.
Card 1/2 approximately outlined. Apparently thesolubility of chromium

SOV/78-4-lo-23/4o
AUT-HORS: Tylkina, M. A., Pekarev, A. I., Savitsk-4y, Ye. If.
TITLEE: Phase D-ia--ram of the System Titanium Hafnium
P~;RIODIICAL: Zhurnal neorganibheskoy khi-,.-,aii,1q5q:'IVo-f-
WZ 0,
pp 232o 2322 (USSR)
~.3STiL~LCT According to data obtained by means of different methods the
phase diagram Ti - Hf was constructed (Fig 1a). As it was to be
ex-oected accordin- to the analogous Structure of the electron
shell of these ele:aents, they form a continuous series of solid
u- and -solutions which are separated by a diphase a+ re.-
gion. Xe curves of the changes of physical properties of
0
the melts with variable composition (Fig 1b) confirm this phase
aiagram. Figure 2 shows the microstructure of titanium - haf-
nium alloys treated in a different way. There.are 2 fi-ares
and 6 references, 3 of which are 5oviet.
ASSOCIATION: Institut inetallurgii im. A. A. Baykova Akademii nauk S33R (In-
stitute of.Metallargy imeni A. A. Baykov of the Academy of
Sciences, USSR)
SU-3YITTED: May 4, 1959
CarA -,/I

67808
.1,D1.2oo so
V/180-59-5-25/37
AUTHORS: Agafonova, M.1 Baron, V.V.9 and Savitskiy, Ye.M.
kmoscow) --------
V
TITLE; Structure and Properties of Niob -Tin Alloys
PERIODICAL: Izves,tiya Akadenii,Lnauk SSSRi~Otdeleniye tekhnicheskikh
nauk, Ketallurgi i toplivo~1959:,Nr 5)PP 138-1 (USSR~
Plate
ABSTRACT: Metallo-ceramialniobium of the following composition
twt X) was use
a s the starting materials Nb 98.11
Ta li2, Ti 0.15, Fe 0 0857 N 0 2) C 0.03i 0 0.2, S1 0.04
and Pb 5.lo-3, and O-i tin (99:9% Sn). The alloys 'were
prepared in an are furnace on a water-cooled copper
hearth, using insoluble tungsten electrodes, in an,
atmosphere of chemi:cally pure argon (0.6 atm-pressure).
As the boiling point of tin lower than the melting
is
Point of niobium, (22800 as against 2415 00,.consid.erable
evaporation of tin occurred on melting. Therefore, 50%
More tin was added to the charge than the calculated
amount
Theare melting method enables niobium alloys
With any tin content to be prepared. The authors have
Card prepared ingots of 22 alloys, weighinglup to 40 9. The
1/6 composition of the alloys is shown in Table 1. In orderL
to ensure a uniform composition the alloys were remelted

-67808--
SOV/180-59-5-25/37
Structure and Properties of Niobium-Tin Alloys.
several times. Alloys containing up to 30% tin were
annealed in evacuated quartz Aouble ampoules in a Silit
furnace at 1100 0C for, 50 hours. Alloys richer in tin,
in view of their lower melting point, were annealed at
200 OC for 100 hours. One part of the alloys
(containing 85-100% Sn) were deformed by approximately
60% by cold forging, prior to annealing. The limit of
solubility of tin in niobium was determined by quenching
and testing the microhardness., Water quenching of the
alloys was carried out in evacuated quartz double
ampoules from the following temperatures: 800 OC, (after
soaking for 100 hours) and 1100 OC (after soaking for
50 hours), Quenching from 1400 and 2000 OG (after
soaking for 20 minutes) was carried out in an apparatus
for measuring melti ng temperatures, quenching from
1800 OC was carried out in the vacuum furnace TVV (after
soaking for 3 hours). Sections for microscopic analysis
were prepared by the usual method. Alloys containing up
Card to 35% Sn were etched in a mixture of HNO and HF (co'nca)
2/6 and those containing between 35 and 100% in in a 30%
aqueous solution of HG1. The microhardness of the.

67808
SOV/180-59-5-25/37
Structure and Properties of Niobium-Tin Alloys
alloys was tested with a PMT-2 instrument, using a load
of 20 g. The hardness of the alloys was tested in a
Vickers hardness testing machine at a load of 5 kg.
X-ray investigations of annealed alloys were carried out
in a Debye camera with a Cu-irradiation. The malting
temperature of the more refractory niobium-tin alloys
was determined by the drop method, using an optical
pyrometer. The temperature was measured at which the
first drop appeared in the drilled-out centre bore of a
specimen; the ratio between the depth and the diameter
of the bore was approximately 1+; this ensured
practically absolutely black body conditions. The
thermal analysis of less refractory alloys (between 30
and 100% Sn) was carried out with a Kurnakov pyrometer
which uses differential registration, in sealed quartz
ampoules. In this case the highest measured temperature
did not exceed 1000 OC. The determination of the rate
of oxidation of the alloys was carried out on specimens
Card of rectangular shape by measuring the gain in weight.
3/6 The surface of the specimen was first ground on a fine
emery paper. Then the specimens were placed in annealed

67808
SOV/180-59-5-25/37
Structure and Properties of Niobium-Tin Alloys
beryllium oxide crucibles and held there for one hour in
air. On the basis of the results obtained, which are
shown in Table 27 the thermal equilibrium diagram of the
Nb-Sn system was constructed (Fig 1). Experimental
results obtained in the investigation of the microstructure
and measurements of the microhardness of the alloys are
shown in Figs 2 and 3 respectively. It has been found
radiographically that the parameter changes In the solid
solution range are negligible, as the atomic radii of the
two elements are very similar. Alloys containing more
than 9.5% tin exhibit a second hase along the grain
boundaries at room temperature fFig 2g), consisting of the
compound Nbj3nj which forms at 2000 OC in the peritectic
reaction. This compound has a complex cubic structire of
the O-W type with a lattice parameter of a = 5.29
is very brittle and has a great microhardness (H
900 kg/mm2),, A further increase in tin content leads to
the appearance of a soft (Hia 10 kg/mm2), low melting-
point tin-rich phase which melts at 232 OC, and
Card subsequently to a separation of the alloy into the molten
4/6 and solid.states (F g 2e, zh, and z) (see Table 2).
I q/

67808
SOV/180-59-5-25/37
Structure and Properties of Niobium-Tin Alloys
No intermediate phases have been observed in the system
by microscopic and X-ray analyses. The solubility of
niobium in tin at the melting point.of tin is less than
0.1%. The hardness of alloys in the reg niobium-
=
2 (for
base solid solutions increases from 150
niobium) to 300 kg/mm2 (at a maximum tin content). In
the 2-phased region,the hardness continues to increase
additively until the Nb Sr4 compound is formed, the
hardness of which is 90; kg/mm2 (Fig 10. The hardness of
tin-rich alloys,is close to that .of tin (9 Wmm2) and
hardly increases with increase in tin content of up to
20% due to the presence of a soft tin-rich phase. In
Fig 5 the results of the measurement of the rate of
oxidation of Nb-Sn alloys in the concentration range of
0-20% Sn on holding in air at 800 and 1000 OC for one
hour) are shown. The results shown in Figs 4 and 5 show
that the alloys in the solid solution range of tin in
have a greater hardness and resistance
to
.
Card oxidation than pure niobium.
5/6 There are 5 figures, 2 tables and 6 references) of which
1 is Soviet, 1 is German and 1+ are English.

i8(6), 21(l) SOV/89-7-3-5/29
AUTHORS: Savitskiy, Ye* M., Tylkina, M. A., Tsyganova, I. A.
TITLE: The Phase Diagram of the System,Zirconium Rheri;,jr.
PERIODICAL: Atomnaya energiya, 1959, Vol 7, Nr 3, pp 231-235 (USSR)
ABSTRACT: By means of the well-~-known radiographiaal~and microscopical
methods the meltiiig point, the hardness, and the microhardness
of the-phases were measured. On the.basis of t-h4_se data -th~
phase diagram of-the zirconium - rhenium system was set up. In.
a-zircon]ium the range of the solid solution of rherlium amounts
to -0.5 % by weight at 6000C. At the eutectic transformatioa
% by weight. In
temperature the percentage increases to 2-3
1
P-zirconium at 160000 14.68 % by weight of rhe-nium 2--id at the
eutect:*Lc point of transformation at 500-6000C only 8 % by weights
are dissolved. In alloys containing,more than 4 % 'ay ws-ght of
rhenium, a stable P-phase is found. At"16000C and 25 % by weight
of rhenium a eutectic forms. In alloys, with a high zlirconi=
content a metastable W ~-phase was found to exist. Tha so!,;!-
bility of zirconium in rhenium at 25000C is less than 2 % by
weight. Three, chemical compounds are produced in 'the system.
Card 1/2 by peritectic r
eactions 1 At 2500OC: Zr5 Re 24 of the a-VIn-t~Yp"e
I

SOV/89-7-3-5/29
The Phase Diagram of the System Zirconium Rhenium
with volume-centered cubic lattice (a 9 6 9 7 kX) Mi cro -
hardnes s amounts to 1000 kg/MM2. 2) At 2450 OC: ZrRe with
2
hexagonal tightly bound lattice (a - 5.21 - 5.25 A*; 0 8.5
.6-56 X; c/a = 1.63). Microhardness 1200 kg/mm2. 3) At 1900OC:
Zr Re d-phase type with tetragonal lattice (a - 10.12 1; c
2 2
5-42 1; c/a - 0.535). Microhardness 700 - 800 kg/mm , The pha5e.
diagram, and microhardness are shown graphically. Photo-
graphs are available forsome of the ground sections. The
radiographic investigations were carried out by P. I. Kripyake-
vich and Ye. I. Gladyshevskiy at the LGU. There are 7 figures,
I table, and 8 references, 4 of which are Soviet.
SUBMITTED: April 16, 1959
Card 2/2

(2,4)
5
,
ZUTHORS: Kopetsk-ly, Ch. V., Shekhtman, V. Sh., SOT/20-125-1-22/67
Ageyev, U. V., Corresponding Member ) AS USSR, Savitskiyy Ye. M.

TITLE: Formation of the 6 Phases in the Rhenium-manganese and
Rhenium-iron Systems (Obrazovani-lye -faz v sistemakh
reniy-marganets i reniy-zhelezo)
~PERIGDICAL: Doklady Akademii nauk SSSR, 1959, Vol 125, Nr~l, Pi) 87-88
(USSR)
ABSTIRACT: Among the numerous known binary and ternary systems of
transition metals 6 phases are o.aserved, i.e. compounds with
an isomorphous structure of the g-u type. According to modern
opinions the condition for the formation of the 6 phase is as
follows: if one of the components belongs to group VII or VIII
of the periodic system the second component must be of group
V A or V1 A. However. the F- phase of the iron-r-henium system
has also a crystal lattice of the 6 phase (Refs 1, 2). Since
the latter system does not correspond to the above-mentioned
cor-d'tion the d_phase car-not be explained within the
.Lramework of the existing theories (Refs 3,:4). The alloy
produced by the authors showed a diffraction pattern confirming
Card 1/2 the data from reference I (Table 1). Lattice temperatures viere:

Formation of the d~Phases in the Rhenium-manganese SOY/20-125-1-22/67
and Rhenium-iron System
/-a 0.5-7.
a 0~92 4.69 and 1-
1
'1234 kg/mmk Put-lications ~ontai-n no data on the following
produ:-.tL2n of -'khe rhenium-manganese alloy. It may be seen from
rcenteenographio results that the a.-mealed (for 360 hours in
vacuam at 10001)) a,'loy Is hoinogenaous and has a lattice of the
phase. Pa7ameter: a = 9.14 1, C = 4.75 c/a~= 0.52
Table 1). The 6 pha-se f-.-rms -from enamel
Fi 1). The

't
servation of 6 phases in the systems mentioned in the title
o
"leacls to in the theoretical explanation
.of the conditions of forra-atlon of these compounds of transition
meta1s. if these, phascs are regarded as a.type of electron

compou-nds
(Ref 3) str-;kes that rhenium similar to manganese
s1hows an anomalous behavior as C-Ompared,to metals of other
CTcups. There are I figurev I table, and 4 reference.-, I of
which is Soviet.
ASSOCIATICH: Ins-~I~.ut -Yrietallurgii im. A. A. Baykova Akademii nauk SSSR
Jnstit,xte rjf.1,',E;+allur6,y imeani A. A~ B a yk o vof the Academy of
S-r-n~-ea, USSPO
.SUBMITTED:~ 1Txiember 7, 1958
Card 2/2

18(7) SOV/2o-126-4-22/62
AUTHORS:' Savitski _Ye. DI., Baron, V. V., Ivanova, K. 11.
TITLE: The Diagram of the Recrystallizati.on of Niobium (Diagramma re-
kristallizatsii niobiya)
PERIODICLL: Doklady kLeademii nauk SSSR, 1959, Vol 126, Nr 4,
pp 771 - 773 (USSR)
A B S T11A C T In the introduction the good mechanicaland physical properties
of niobium are stressed, and determinatiorL of the recrystalli-
zation temperature of-niobium and the investigation of the,in-
fluence exercised by 11 alloys upon the beginning of recry-
stallization are given as the task to be achieved by this paper.
Treatment of the bars of 29 mm diameter and 120 mm length, which
was carried out forthe purpose of eliminating the coarse
structure, and by means of which a fine-grain polyhedral struc-,
ture was obtained, is described. It was found that the plastic
properties of niobium improve considerably after annealing, and
a recrystallization diagram is shown, from which the dependence
of grain sizes.on deformation and on the annealing temperature.
may'be seen. Determination of the beginning of recrystalliza-
tion was, carried out by means of X-ray methods. It was found.
that the temperature of the beginning.of recrystallization de
Card 1/2 creases from 12000 to 1025'C with increasing deformation. De-

The Diagram of the Recrystallization of Niobium, SOV/2o-126-4-22/62
terminationof hardness at dejormations of up to-80% showed
an increase of from 135 kg/mm at 0,% to 165 kg/mm2 at~Wla.
Further, the dependence of:grain sizes onthe annealing temper-
ature is-discussed and the critical decree of,deformation at
a ?
an annealing temperature of, 1300 is given as amounting to
7.5%. In this case Ia Grain size of 251 was obtained. From
the results obtained the conclusion is)jd'rawn that the most
favorable.thermomechanical treatment of niobium may be carried.
out within the temperature interval of 1100-14500C and with a
degree of deformation exceeding 10%. There are 3 figures, 1
table, and.7 references, 2 of which are Soviet.
'ASSOCIATION: Institut metallurgii im. A. A. Baykova Akadenii nauk SSSR
(Institute of Metallurgy imerii A. A. Daykov of the Academy of
Sciences, USSR)
PRESENTED: February 25, 1959, by P. A. Re-birideri-Academician
SUBMITTED: February 14, 1959
Card 2/2

24(2) SOV/20-127-2-21/70
AUTHORS: Tylkina, M.A., Kirilenkq R. Savitskiy, Ye, M.
TITLE: The Diagram.of Recrystallization of Hafnium
PERIODICAL: Doklady Akademii nauk SSSRf 19599 Vol 1279 Nr 2, PP 310-312
(USSR)
ABSTRACT: It is the object of.the present study,to determine some of the,
properties of hafnium and to investigate recrYEtallization- and
deformation-processes. From metallographic and X-ray analyses,,
as well as by determining hardness, the authors derived the
recrystallization diagram shown in figure 1. Hafnium is a
dimorphous metal, the hexagonal 04-modification changing in-to
the cubic body-centered A -modification at higher temperatures.
Hafnium iodide bars of coarse structure were used as original
material. The physical properties of these Hafnium iodide bars
are given together with a description of the elimination of the
coarse structure. The deformation was carried out in eight steps-
from ranging 50 to the maximally tolerable deformation of 60~6.
Vacuum-annealing was performed in seven stages between 750 and
Card 1/3 15500 c Recrystallization set in at 10000 C after 10%

Th-e Diagram of Recrystallization of Hafnium SOV/20-127-2-21/70
deformation,at 8500 C after 201,7v' deformation, and at 7500 C
after 40% or more deformation. Annealings within the tempera-
ture range of the *,e -modification yield a fine-grained
polyeder structure with grain sizes of between 25 and 40,,,&-
after 30% to 45% deformation. Annealings above the temperature
of the polymorphous transition gives a coarser grain (240~)
and a marked structural change. The similarity of the
deformation- and recrystallization properties,between hafnium,
titanium and zirconium is pointed out. Also, theirod - and
~_modifications are compared and their high plasticity
stressed. By their hardness andleold workability they are
arranged in the following order:.titanium - zirconium
hafnium. It follows from the recrystallization diagrams of the
Card 2

The Diagram of Recrystallization of Hafnium SOV/20-127-2-21/70
three metals that they also have similar grain sizes.
Finally, the temperature stability of these metals and -their
alloys is emphasized. There are 3 figures and 11 references,
6 of whic h are Soviet.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(institute for Metallurgy imeni A. A. Baykov of the Academy of
Sciences, USSR)
'PRESENTED: March 26, ,195,0, by I. P. Bardin, Academician,
SUBMITTED: March 25, 1959
Card 3/3

0 D 66456
'AMORS., Ageyev, N. Ve, Corresponding MemberAS USSR, BOT/20-129-3-24/70
Kopetakiy, Ch. V.9,-Savitakiyj Ye* M.v
Shekhtmonq V. Sh.
TITLE: On the Interaction of the Elements of the VIIA Subgroup With
Transition Metals
FIRIODICAL: Doklady Akademii nauk SSSR, 1959, Vol 129, Nr 3v PP 559 562
(USSR)
.ABBTRACT: Nn is known to belan anomalous metal with regard to combining
forces between the atoms, the crystalline structure, etc.
(Refs 1,2). Active interaction with the elements of the sub-
groups IVA, VA, and VIA is typical of rhenium. In connection
herewith, 6- and X-phases are formed in binary systems ,
(Refs 3,4). Mn and Re are anal6gous with regard to the form&-
tion of oxides, acids, etc. It ieq however, unknown whether
they are analogous with regard to interaction with metals.
Table 1 shows distinct differences of the physical properties
of Mn. Re, and~Tc. Great similarity of Kn and Re an to the for-
~mation of metallic phases can be soon in analyzing~tho int*rac-
tion of Un and Re with transition metals. Figure I shows the de-
Card 1/3 pendence of the value of the dimension factor (razmern~y faktor)P

66456
-,On the Interaction of the Elements of the,VIIL Subgroup SOV/20-129-3-24/TO
With Transition Metals.
(with regard to Mn and Re) on the group number of the periodic
system for all transition metals (Ref 6). Figure I shows the
compounds formed with a corresponding transition metal in a
binary system of Un or Re. Mn and Re and the above elements of
the subgroups IVA and VA form Laves phases with a structure of
the type MgZn 2 and .MgNi2 (ZrRe 2' ZrMn2 T'NA2 T&*n2'Nbnn2 ). All
these compounds are formed from the liquid phame and are stable
up to room temperature. It may be concluded therefrom that there
exists great similarity between Mn and Re in the formation of
alloys with transition metals. This is, provedl above all9 by
-the type of interaction with elements which are at right and at
the left of group VII in the periodic system. Compounds are.
formed with the metals of the subgroups IVA, VA, and VIA. Solid
solutions on the basis of more simple structures or compounds
with a simple structure, however, are formed with metals of
group VIII. In binary systems, Un and Re form the same type of
phases with the metals of the titanium-, vanadium-, and chromium
group. Mn and Re show a great tendency towards formation of
/3 6-phases. The structurecorreeponding to the low-temp 0
Card 2

66456
On the Interaction of the Elements of the VIIA Subgroup SOV/20-129-3-24/TO
With Traneition Metals.
&m9 of Kn.ie formed am an-independent compound in systems w
h
P
Re basis. Since there are-no papers av ailabl e on Te alloys, the
binary systems can not be completely classified on the basis of
subgroup VIIA. It may be assumed.that To reacts in alloys in a
similar way an Re. The comparatively d4stinct classification of
the binary systems of-transition metals with Nn'and Re as well
as a restricted set of phases existing in these systems are ob-
viously related to the key position of subgroup VIIA amiong'tran-
sition-metals. There are I.figure, I table, and Treferences,
3 of which are Soviet.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akadenii nauk SSSR
(Instituie of Metallurgy,imeni A.-A. Baykoy,of the Academy op
Sciences, USSR)
SUMITTED: August 12, 1959
Card 3/3

ta.

'vt

At

VIP I
Ag
AN
14
IL

SAVITSKIY, Ye.M., doktor khim.nauk, otr.red.; SHAPOTALOV, I.K., red.;
'"KAMAYBUS O.M., red.izd-va; ISLEENTIYETA, P.G., tekhn.red.
[Rare metals and alloys; transactions of the First All-Union
Conference on Rare Metal Alloys, November 18-20. 1957] Redkie
metally i splavy; trady Pervogo Vaesoiuznogo soveshchaniia po
splavam redkikh metallov. 18-20 noiabria 1957 9. Noskva, Gos.
nauchno-tekhn.izd-vo llt-ry po chernoi i tavetnoi metallurgii,
1960. 404 P. (MIRA 13:6)
1. Akademiya nauk SSSR. Institut metallurgii.
(Metals, Rare and minor) (Rare earth metals)
------- ----- -- -

PHASE I BOOK EXPLOITATION SOV/4164
Vsesoyuznoye soveshchaniye po splavam. redkikh metallov. Ist, Moscow, 1957:
Redkiye metally i splavy; trudy... (Rare Metals and Alloys; Transactions of the
First All-Union Conference on Rara-Metal Alloys) Moscow, Metallurgizdatv 1960.
438 P. 3,150 copies printed.
Sponsoring Agencies: Akademiya nauk SSSR. Institut metallurgii; USSF
Komissiya po redkim metallam pri nauchno-tekhnicheskom komit6te.
Ed.: I.K. Shapovalov; Ed. of Publishing House: O.M. Kamayeva; Tech. Ed.s
P.G. Islentlyeva.
PURPOSE.- This collection of articles,is intended for metallurgical engineers,
physicists, and workers in the machine-building and radio-engineering industries.
it may also be used by students of schools of higher education.
COVERAGE: The collection contains technical papers which were presented and dis-
cussed at the Firot All-Union Conference on Rare-Metal Alloysj, held in the In-
stitute of Metallurgy, Academy-of Sciences-USSR in November 1957. Results of
investigations of rare-metal alloys, titanium 3and copper-base alloys with ad-
ditions of rare metals are presented and discussed along with investigations of
rhenium, vanadium, niobium_,and their alloys. The effect of rare-earth-metals

Rare Metals (Cont.) SOV/41614
on properties of magnesium alloys and steels is analyzed., The uses of rhenium
as a dehydrating catalyst, electroplating material, and material suitable for
making plugs for automobile electrical systems are discussed. Also, the ef-
feet of the addition of certain elements on the properties of heat-resistant
steel is examined and alloys with special physical properties (particularly
semiconductive alloys) are discussed. No personalities are mentioned., Soviet
and non-Soviet references accompany some of the articles.
TABLE OF CONTENTS:
Opening Speech of A.P. Vinogradov, Member of the Academy of Sciences USSR
The Letter of I.P. Bardiny Member of the Academy- of Sciences USSR 5
PART 1. THE PRESENT STATE OF INVESTIGATION OF
RARE41ETAL ALLOYS
Savitskiy. Ye.M. The Present State and Problems of Investigations of Rare-,

Rare Metals (Cont.)
PART III. WMIUMI VANADIUM, NIOBIUM,
ZIRCONIUM AND ALLOYS BASED ON,THEM
Balandin, A.A., Ye.l. Karpeyskayaj and A.A. Tolstopyatova. Rhenium as a
Dehydrating Catalyst 72
Tylkina, M.A., and Ye.M. Savitskiy. Rhenium Alloys 80-
Sklyarenko, S.I., Z.M.,Sominskayag A*A. Nikitinynd I.I. Lavrov. Electro-
plating With Rhenium ill
Usov, V.V., and M.D. Povolotskaya. Electrical Contacts Made of Rhenium 123
Shumskaya, Ye.A. The Possibility of Using Alloys on Tungsten With'Rhenium
ror Making Contacts for Automobile Electrical Equipment 133
Baron, V.V., and Ye.M. Savitskiy. Properties of Vanadium, Niobium and of
Alloys Based on Them 136

'Rare Metals (Cont.) SOV/4164
Andreyeva, V.V., A.I. Glukhova, Ye.A. Kamenskaya, L.I. Seleznev, and M.V.
Malltsev. Corrosion Resistance of Zirconium and Its Alloys 156
PART IV. RARE-EARTH METALS
AND THEIR EFFECT ON PROPERTIES OF MAGNESIUM ALLOYS
Ryabchikovp D.I., and Yu.S. Sklyarenko. Rare-Earth Elements and Possibilities
of Producing Them 171
loffe, V.M., V.M. Bagayeva and L.M. Pedyash. Production of Alumlmm-Cerium~
Aluminum-Lanthanum., Magnesl;~Cerium, Magnesium-Lanthanum., and Magnesium-
.Neodymium Addition Alloys by Electrolysis 180
Terekhova, V.F., and Ye.M. Savitskiy. Investigation of Physicochemical
189
Interaction of Rare-Zi~rte ~as Mh Magnesium, Iron, Chromiumfnd Titanium
Mikheyeva, V.I.I.and M.Ye. Kost. Hydrides of Rare-Barth Metals and Possibi-,
lities of Their Practical Utilization 202

A: 1:~ I
0 D 1 CI At annaya Vnc-rZ lYa, V no 96 1 , .10 410~
^7 Ya ;~o ~"k Z, -,4- e -~kor~ a Fi--, a izu
~7V an by th-.~
1himili ir-n. N. 1.
Izio, --ut o~"!` C~:cy A
if 7-nori-,ania 3. Furnakov, AS USSR)
~r,,) %li-3 lnt)tltut ci~~tulliArrli in. A. A. ESSR (Inctituta 0.1
in.)nl A. A. P from 6 tt) IQ,
'I'l 'he oca"Inion of --a 100:1i jmnlvcro,~vy a.' the bir'.111.1ay a!
if~zrnnkov. Pnr' of tho #.!12 r~~pjvrtj mnde nt the Cane-)rnnoa drialt ivith
Probl,ma of thu atomio friduritr:,, reporta on th-'~ phys-lao-chmical
c,nalysj5 ot . thrrium, uranium, plutonian. vnd 01"!r a3 -,,all as of
7irconiun and S. 11radiation ~ihenom-:?nrt and ne-ft
r-roblems oz phyzico-oheraical nzialyoj2" (V. 1, Soit ---n); rtruct:;re and
("oIrrtizzit"On d, 11 i7rnma of the t-~,rnary uy3tems thorium - zirconium - uranium
(G. K. Aleknoyenko and T. A. Dnd--iyova), uraniur - =~il,.blenu- - 'zirooniu13
uran."im - zironium n`oblur; (L. 1. uranillm
Y
n' and ph.73T~---ch,-miunl analyr.1-9 of,
nyatcm with rare metain v- Snvit-Icil"'. V. F. Torekho-.,a
~,~portod axnerimental imd theartl1i7:n7t 'In rairi-earta Iloya and
Pr-'rented ne- conatitittion dingrams of alloja of yl*.rium, necdynium, and
gc, dolinium with zin6-nLsiam, of,Yttriun and neadyn-Jum with aluminum. and
gadol"niun wia !ran and aickel; f-artharmore, ;~h~) described the
propertieti of 'he jattLr. M. A. Tylkiria h~~-Ld a reporl 0.1 tests of alloys
Of rhrium, tantalum, and tungaten, and alao Or, r~-actiona between these
nd 8th group.
alloys and elements of the 4th, 5th, 6th, 7th, a.

SAVITSKIY, Ye. M., and TUMA, M. A*
Certain Physical Properties of Rhenium and Its Alloys
E. M. SavitBki and M. A. Tylkins, The Institute of Metallurgy of the Academy of
Sciences of the U.S.S.R.0 Moscow, U.S.S.R.
Studies have been made of recry-stallization of rheniim, and of alloying with
tungetenj, nickel (in Ni-Cr alloys)~ and with titanium ond its alloys. Rhenium
additions improve both room and elevated temperature properties and increase the
initial recrystallization tenperatures. Solid solution tungsten alloys have
increased workability and electrical resistance. Applications for rhenium alloys
are promising for thermocouples, electrical contacts and scme vacuum tube parts.
Results are given a study of rheniwn as a contact material.
Report presented at the 117th Meeting of the Electrochemical Society, Chicago#
1-5 may 196-0.

SAV-1TSKIY, Ye. M., and TYLKINA, M. Ae
Rhenium and Transition Metals Phase Diagrams
E. M. Savitski and M. A. Tylkina, Institute of Metallurgy, Academy of Sciences of
the U.S.S.R., Moscow, U.S.S.R.
Binary phase diagrams of rhenium with titanium, zirconium., hafniums vanadium.,
nibblum, tantalum, chromiumll molybdenum, tungsten, manganese, and cobalt have been
determined. A number of these alloy systems are characterized by the formation of
inter-metallic phases of the sigma or alpha-manganese types. Comparisons are made
of these and other common features of the respective,diagrams on the basis of the
periodicity of the binary alloy additions.
Report presented at the 117th Meeting of the Electrochemical Society, Chicago,
1-5 may ig6o.

KRIPYAKEVICH, F.I.; TYLKINA, M.A.; SAVlTSKIY, Ye.M.
New compound in the rheaium-zirconium s7stem and its ar7stal
structure. Izv. vys. ucheb, zav.; chern. met. no.1:12-15 160.
l.Livovskiy gosudarstvennyy universitat i Institut metallurgii
AN SSSR.
(Rhenium-zirconium alloys--Metallograph7)

E091/B 255t
UY21H.ORS SaviLlskiy, Ye. M, Terekhova, V., F., and Naumkin, 0. P
DITLE ium and its Alloys
!ODICAL- Tsve -IM35e me tally 1960. Nr 1, pp 43-48 (USSSIP)
'ABSTRACTS The a-uthors~have investigated the pbjsico-mechanical
properties of erbium and its reaction with a few of the
meLalp commonly met in industry. Theseeinvestigations
.are a'continuation of a cycle of published studies, carried
out at the laboratory of rare metal alloys of the
Institute of Metallurgy, AS USSR on the physico-c-hemical
PrOT)ert2es. of rare earz metals and their alloys
(Refs '5 to 8). Metallic erbium. of 99,3_r-.,% puTity was
used for the study. It'contained the foillowing chief
impurities: lTd; 0,1%,- Ho 0.28%,, Tu 0,1106, Y 0~1%~
J
Th 0,2%, Ca 0.022%. Fe 0.01% and Ou The micro-
,Lre of the or
struct 'isinal cast metallic erbiura is shown
in Fig- 1, The hardness of metallic erbium (H ) is
to 135 kg/mm2 (Vickers),, Its hardness af er remelting
In an argon atmosphere rose by,10 to 15 kg/mm The
densi t,-,f of erbium.was determined by a hydrostatic method,
ard anti -also by X-ray, analysis., The result's were respect4
_Lve ly

nu

6, Qo
E091/B255
_nq and its Al-
oys,
area was observed., The authors have studied the physico-
chemical reaciti-ions of erbium with the basic components
of industrial alloys - Mg, AL; Fe I Ti and Ta. Alloys
were cast of the above metals with additions of 5 wt.%
er'bium, Fig 3 shows.the microstructure of an Al-50/6
erbi= alloy, Fig 4 that of an Fe--5% erbium alloy and
Fis 5, that of a tantalum-erbium alloy, It was found
that erbium in quantilties of 50% can be melted with Al,
DIg, Fe and Ti with the formatlon, in all cases, of
2-Dhased.mixtl-urea of the eutectic of peritectic type
J fier
For all inves.tigated alloys, erb-um is a good mod-.L
and strengthener. It does not alloy with Ta. As erb-11M
is extremely rare and expensive, it cannot,be used as
an alloying element for industrial alloys. Its fields
of application can be in construction of special
ins-Uruments, in eler,,tronic apparatus and in other
directions where its Particular,physical properties
(eg ferromagnetism..optical properties, etc) can be
exr,loited. The, fur'ther study,of erlbiimri and its alloys
mi.ist concentrate on.-the complex of physico-chemical
Card 4/5

68687
/.2 00 3/130/60/000/01/009/02?
-EO71/E-135
AUTHORS: Baron- V. Yefimov, Yu.V., and Savitskiy, Ye.K.
Moscow)
TITLE, The Structure and Properties of Alloys of the ianadiiam-
ZSten System
Aga
PERIODICAL. Izvesti.p.Akademil nauk SSSR.Obdeleniye-tekhnicheskikh
nauk9 Metallurgiya i toplivo, 1960,Nr 1, pp 70-74 (USSR)
ABSTRACT: The microst.ructure, hardness, plasticity, strength and
susceptibility to oxidation of vanadium-tungsten alloys.
,in the whole_range of concentrations was investigated.
The following starting materials were used:
vanadium, '98.6% V1 0-3~- c, 0-591,' oxygen, 0.29o' nitrogen,
0.06% sulphur and less than 0.2% of metallic admixtures;
tungsten-. 99.951/c Wo, 0.032% Mo, remaining oxygen and
nitrogen. About 40 g samples of alloys were melted in
an are furnace with non-consumable tungsten electrodes in
a medium of helium under pressure of 0.5 atm. In all
cases the content of tungsten was 1% higher than in the
Card starting charge. Cast alloys were annealed at 1100 00
1/3 for 500 hours in double quartz sheaths, evacuated and
sealed. Specimens forthe investigation were prepared,

68687
S/180/60/000/01/009/027
EO?I/EI35
The Stmucture and Properties of Alloys of the Vanadium-Tungsten
System
by a-node cutting with subsequent polishing. The
solidus temperatures were determin d by the
I e drop method,
,metallographic and X-ray analyses by the usual methods,
hardness by the Vickers apparatus, plasticity and
strength on compression of specimens 4 x 4 x 6 mm in a
"Gagarin" press, and the suse.,,eptibility to oxidation on
hsating in air by the gravi-metric method. (increase in
weight, or deerease in weight after mechanical or
chemi-al removal of the scale formed). In some cases
the scale was chemically analysed. On the basis of the
results obtalned. the equilibrium diagram of the system
vanadium-tungsten was !~onstructtad (Fig 1.). Vanadium
and tungsten form a -continuous series of solid solutions.
The solidus and liquidus curves possess a sharply
expressed mlinimlim at 4-5 at,% of tungsten equal, to
1635 0G. However, no transformations in the solid state
Card in allo-,rE. corresponding to th-is section of the diagram,
wz-re obzerved. Small additions of tungsten to vanadium
ot the a~bove quoted purity) oause an increase in

68687,
S/180/60/000/01/009/027
E071/E135
The Structure,and Properties of Alloys of the Vanadium-Tungsten
System
plasticity, a decrease in hardness and a small increase
In thecompression strength.. Further increase in the
content of.tungsten causes changes in proper ties,
characteristic for systems with continuous solubility
in the solid state. VaniLdium. decreases the resistance
of tungsten to oxidation. At temperatures between 700
and 1100 OC all alloys as well as startingmetals- are
strongly oxidised and require protection (Fig 3). The
microstructure of annealed vanadium-tungsten alloys is
Card shown in Fig 2.
There are.3 figures and 2 references, of which 1 is
3/3 English and 1 is German. There is also a table (p 70)
SUBMITTED: July 21, 1959*

DASHKOVSKIT, A.I.; YWSTYMIN, A.I.; SAVITsi-l-y-,--Y-e-;w.-

M., SKOROT, D.M.
DASHKOVSKIT, A.I.; YEVSTYUKHIN, A.I.; ~-SA Te

80981
18o/60/000/03/013/030
S/
AUTHORS: Savitski E12?4~38ad Terekhova, V.F.(Ploscow)
a
Ye.M., Stepanov,
.TITLE-, NVNeodymium and Its Alloys with Aluminium
PERIODICAL: Izvestiya Akademi! nauk SSSR. Otdeleniye telchnichoskikh
nauk, Metallurgiya i toplivo, 1960, Nr 3, pp 73 - 78 (USSR),,
ABSTRACT: The object of the present investigation was to determine the
physical and mechanical properties of pure (99.50,60) neo-
dymium and neodymium-aluminium alloys. The following
properties were determined for cast neodymium: Brinell
2
hardness 46 kg/mm ultimate compressive strength
2
25 kg/mm ductility (in compression) It has
been found that neodymium. is characterised by good. both
hot and cold, workability, it being possible to produce
neodymium strip, 0.5 mai thick, by cold-rolling with
0
intermediate annealings at 500 - 600 C. Neodymium,
cold-rolled to 70~ reduction in thickness, had the UTS
equal -to 13 k9/MM and ductility (in tension) equal 1-2%.
The constitution diagram of the dluminium-neodymium system,
constructed on the basis of metallographic and thermal
analysis, is shown in Figure 3. It has been found that
Cardl/3

s/18o/6o/ooO/03/0l3/O3O
Pla/E383
Neodymium and Its Alloys with Alumin3.
solid solubility of neodymium in aluminium does not
exceed 0.21". A eutectic, containing approximately
10 1 0
13 wt-0.0 neodymium, is formed at about 640 C. In.the~.
investigated concentration range- the existence of.two
intermetallic compounds, NdA14 and NdAl2 , has been
observed. The former is formed as a result of a peritectic
reaction at 1 250 OC;.the latter crystallizes out from the
liquid phase at 1 450-0C. Owing to Ithe formation of the
intermetallic compounds, addition of neodymium to
aluminium increases the strength of the latter metal.
Hardness of an alumi-ni., -base alloy.containing 30 ~[t-%
im
neodymium is .155 kg/mm , as compared -with 25 kg/mm for
pure aluminium; addition of 5% neodymium increases the
2
UTS of aluminium from 5 to 10 kg/mm and lowersits
ductility by 5-10%. Hardness of the Intermetallic compounds
2
NdA14 and NdAl 2 is 350 and 00 kg/mM , respectively.'
The electrical restivity of aluminium is not significantly
'Card2/3 'fected by addition of neodymium; resistivity of the
af

80981
S/180/60/000/03/013/030
E193/E383
Neodymium and Its Alloys with Aluminium
5'1~; Nd-,Al alloy �s practically equal to that of pure
0
alumInIum. The effect of temperatur-e Up to 300 C on
the mechanical properties of the Al- Nd alloys with up
to 50,,a' Nd has been also investigated. Figure 1 shows
the microstructure of neodymium (a) cast, (b) after 700/0'
cold deformation and aftercold deformation to 700/",
and annealing at 500 C. Figure 2 shows the microstructure
of the aluminium-neodymium alloys (cold-worked and
annealed), containing 0. 0.74, 1.05, 9.24, 24.21, 47-47
and 660,,a' neodymium. There are 3 figures 2 tables and
9 -references, 7 of which are Soviet and 2 English.
SUBMI7TED- blarch 2. 1960
Card 31-,

82628
s/18o/60/000/004/023/027
Elll/E'*52
'AUTHORS,.- Baron, V.V-I lvanova,,_K~N. and Savitskiy, Ye.M.
(Moscow) -------------------------
TITLEs Phase Diagram and Some Properties of.Alloys of the
system Niobium-MolybdenuLm-v
PERIODICALt zvestly'a Akadl' Otdeleniye tekhnicheskikh
emii nauk SSSR
nauk, Metallurglya i toplivo~ 1960q No.4, pp.143--149
+ 1 plate
TEXT3 The microstructures in the as-cast and annealed states
(Fig.1), hardness (Fls.2.5), melting points (table) were
determined for the ternary Nb-Mo-V (and corresponding binary)
systems. The solidus isotherms are projected on the tr�angular
diagram and the corresponding binary fusion diagrams.are-plotted
in Fig.3. , A continuous solid-solution range for the ternary
system was found. The solidus-isotherms show that the fusion
temperature of the alloys falls (from 2450 to 1800*C) as the
vanadium rises.' . At the niobium corner of the diagram, alloys
had the lowest hardness'(105 to 220 kg/mm2). The oxidation of
thealloys at 1000 to 12000C was also studied: specimens were
placed in crucibles pre-ignited to constant weight, the gain in
Card 1/2
----------

82628
s/i8o/60/000/004/023/027
Elll/E452
Phase Diagram and Some Properties of Alloys of the System
Niobium-Molybdenum-Vanadium
weight for 1 hour's heating in air being determined. The results
Ashown by curves 1tv" in Fig.2 and 4) indicated that the best
resistance to scalInf is possessed in the binary systems by
5% Moo 5% V (at 1000 C) and 15.4% Mo, 2.4% V.(at 1200 C); and in
the ternary by alloys with 5% Mo, 2.8% V and 5% Mo, 5.6% V, which
also have other advantageous properties. A common feature of all
alloys with high molybdenum and vanadium contents is a high
oxidation rate. Variation of hardness with composition in binary
and ternary alloys corresponded to property changes c haracteristic
for a continuous series of solid solutions. Variation of scaling
resistance with composition does not show such a relation. In
general, increase in scaling resistance of the ternary niobium
alloys occurred at,a lower degree of alloying than with binary
alloys. Some ternary alloys,oxidized faster at 1000 than at,
1200'C There,are 5 figures, 1 table and 8 references-,
3 Soviet and 5 English.
SUBMITTED8 April-1, 196o
Card 2/2

S/50q/6o/ooo/oo4/oiq/O24
C021/M6
AUTHORS: Savitskiy, Ye.M., Tylkina, M.A.O.IpatoVas S.I.,
and Pavlova, Ye.I.
TITLE: Physico-Mechanical,Properties of Tungsten and,
Rhenium
PERIODICAL: Akademiya nauk SSSR. Institut metallurgii.
Trudy, No.4, 1960. Metallurgiya, metallovedeniye,
fiziko-khimicheskiye metody issledovaniya, pp.214-229
TEXT: Rhenium has been suggest Ied,.as a possible alternative
for tungsten for use in the electro-vacuum industry, but it is
very expensive. Therefore an investigation of tungsten-rhenium
alloys.was carried out. Alloys were prepared in an arc furnace
and by powder metallurgical methods. The complete range of
alloys was studied by metallographic and X-ray analysis, by micro-
hardness measurements and by measuring melting points. The
formation of the compound W2Re3 (cr phase) in the region 48-65 wt,-%
rhenium and the formation of a eutectic between the cr phase and
,the rhenium solid solution at 75 %it.% rhenium and 2815 OC were
and tungsten was found.
,confirmed~ No eutectic between W2Re3
Card 1/4

S/509/60/000/004/oig/o24
E021/EI06
Physico-Mechanical Properties of Tunssten and Rhenium
There was a wide range of solid solutions of rhenium Iin tungsten
(up to 30%) at high
temperatures
, with decreasing solubility as
the temper* _
ature was decreased. The compound WpRe3 formed by a
reaction possessed a
peritectic high hardness (about 2000 kg/mm2)
-
and was,brittle. A method was developed for preparing wire of
diameter 12 microns from alloys with a maximum rhenium content of
20 wt.%'. The wire was prepared by hot-working samples prepared
by powder metallurgical methods. The introduction of rhenium into
tungsten raised the temperature of the beginning of recrystalliza-
tion by 200-400 OC depending on the rhenium content. Grain growth
of tungsten-rhenium alloys was l ess intensive than that of
tungsten. The tungsten-rhenium alloys.retained a high strength
and possessed considerable ducti lity after annealing at 11100-
1950 OC. The initial strength of 100 micron tungsten wi re was
320 kg/mm2 with an elongation of 1-50%.
After heating at 1950 OC
the strength decreased to 80 kg/ .
mm2
S and elongation was 0. The
alloy containing'21% rhenium in these conditions decreased in
strength from 370to 150 kg/mm2 and the elongation increased from
Card 2/4

656.39
S15 09/ 6 0/ 000/004/019/024
E021./8io6
Physico-Mechanical Properties of Tungsten and Rhenium
1.5 to 6-8510. After -annealing Iat i4oo-15,00 OC~, the strength of
this alloy was 1807190 kg/mm2 and its elongation A-2oa%. The
strength of wires of the alloys was higher than that of tungsten
wires at all temperatures, although an increasein temperature
resulted in a decreas'e in strength. At 1400 OC the U.T.S. of
was 42 kg/mm2 and that of an alloy containing 190 rhenium
tungsten - 16
was 66.7 kg/MM2. At 26oo OC the figures were.4 and 6.7 kk/mm2
respectively. The limiting testing temperature of alloys
containing 10 and'2056 rhenium was 3000 OC, or 3000 higher than the
limiting temperature of tungsten or alloys containing I and 3%
rhenium ' The hardness of cast tungsten-rhenium alloys was
tested in the range 20-1000 OC. At 8000C alloys containing
10 25 and 755/a rhenium and pure rhenium had a hardness of about
20; ks/mm2. Tungsten and alloys containing 101,10 rhenium had a
hardness of 100 kg/mm'-. , The electrical resistance of 50-micron
wires of the alloys was measured at 20 to 1350 'C. I At any given.
temperature the resistance was higher with higher rhenium contents.
Card 3/4

S/5oq/6o/ooo/004/Olq/024
E02-1/Eio6
Physico-Mechanical Properties of Tungsten and Rh enium
At 20 OC the resistance of tungsten was 0.056 ohm. mm2/m, and that
of the alloy. containing 21.1,-,') rhenium was 0.2112 ohm, 1111112/m
At 1600 OC the resistances. were 0.114 arid U.644, ohm.mm2/m
respectively. Thus the tungsten-r.henium alloys possessed several
advantages over tungsten.
There are 11 figures and 23 references. .19 Soviet and 4 English.
Card 4/4

8
S/509/60/000/004/020/024
EIII/E152
AUTHORS: Savitskiy, Ye.M., Baron, V.V,, and Yefimov, Yu.V.
TITLE: !'has eDiagram and Properties of Vanadium-Chromium
Alloys
PERIODICAL: Akademiya nauk SSSR. Institut metallurgil.
Trudy,, No.4, 1960. Metallurgiya, metallovedeniye,
fiziko-khimicheskiye metody issledovaniya, PP-230-235
TEXT: The authors describe their Work on the vanadium-
chromium phase diagram. Their starting~materials were:
alumino-thermic vanadium (95-50" V, 1.0 Al, 0.15 Fe, O.2,C, 0.3 Si,
considerable concentration of' oxygen) and electrolytically refined
chromium (99.90,-D' Cr, 0.02~Fe' 0.03 Si, 0.02 N,0.002 H, 0.0023 0).
Alloys were are melted (non-consumable tungsten electrode) under
helium, each ingotof 50 g being remelted four times and analysed.
Compositions of the charges and alloys are shown in the first two
main columns of a table. Solidus and liquidus temperatures were,
determined under argon in an apparatus constructed in the
Laboratoriya splavov redkikh elementov IMET AN SSSR .(Laboratory o .f
Alloys of Rare Elements, INIET AS USSR). Specimens were heated'by-
Card 1/4

S/509/60/000/oo4/020/o24
Elll/E152,
Phase Diagram and Properties of Vanadium-Chromium Alloys
current from a type ok-Y-4o (OSU-40) Lransformer-, temperature was
determined with an optical pyrometer calibrated under similar
conditions against melting points of pure nickel, titan3i
.um'
zirconium, niobium and molybdenum. Liquidus temperature was the
,reading when the specimen lost cohesion, the solidus, that when
a hole drilled in the 4 x 4 x 15 mm specimenfused over. 1 1 1. ~ V
.Curves 1 and 2 in Fig~l show plots of these temperatures against
wt.5fo Cr (thi relatively low value for vanadium is due to
impurities). Microstructure was studied and hardness measured on
the cast alloys and alloys annealed for 100 hours at 1100 OC in
evacuated quartz capsules and slowly cooled. The hardness (Hk,
kg/mm2) results are shownin Fig.1; curves III and IV correspond
t
to the cast and annealed states respectively, and curve V gives
hardness at 1000 OC (annealed alloys). Hardness was determined
h
with a 50-ks,load on a "pobedite" cone, in argon at the high-
~
temperature which was measured with -a Pt/Pt-Rh thermocouple.
Electrical resistivity of annealed 4 x 4 x 15-20 mm specimens was
,determined potentiometrically at room temperature, results are
C
Card 2/4

~A
T
4%,

PU-G
ad O-Td
-
0 UM.XS-eTa

f'o-(rv eA 5
oxTlo-UMTP'cu
um"Flu

605/9
00/000/09/
IIZO/OZO/ll

86,o63
I g. 1.200 4 r4 S/180/60/000/005/004/033
Elll/El3c
AUTHOR: Savitskiy, Ye.,M, (Moscow)
TITLE: ke~a~lsin He-E-M-Resisting Alloys
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye -tekhaicheskikh
nauk, Metallurgiya i toplivol 19609 No. 5, pp.52-69
,TEXT-, The author carried out much work (e.,g ' Refs 2, 3j 18)
and 34) on rare metals and alloys of them, In the present paper,
using published information, he discusses possibilities of using
re metals as bases for heat resisting alloys, and their,effec-1- on
.ra U
heat-resisting alloy properties~. Table 1 shows the main physical
.and me---hanical properties'of high-inelting'metals and draws some
general conclusions for discussion, while Table 2 gives
solubilities of carbon o e nitro en nd hydrogen some of
Ju
these metals, The a thg goens7J4oE to ~diuss theprope ies of
.alloys based on -individual.rare metals. The first is1rhenium, which
,--he author considers reliably established as the only component for
good me-hanical properties at 2000-3000 OC, Tantalum. is another
promising alloy base but, like rhenium,,-,;I* e.'-IN!obium s more
is scare
P'en'iful, but liable to oxidation', while vanadium tLas a tively
.~ow melting.point, Hafnium and zirconium are contidered by the
Card 1/3

36o6l
S/180/60/000/005/004'/033
EllI/El35
Rare Metals in Heat-Resisting Alloys
ai,~thor t~nsuitable as bases for very high-temperature alloys, but
ha~,ring good corrosion resistance,-v'~Yttrium has some advantageous.
_pro -rtips. t The author. urges furtfiTr-judies on this element and
On'ku_t-etiu m_.Athuilium, '\erbi scandium. In the
3e.:~ t i I , -LblumAholmium and-It I
_on on the influence of rare metalson eat-resistjIS-al-loy
proper~ienn, the. author discusses the -following possible effects:
gra A refining of the alloy base (pure meta! or solid'solution
based on it) as exemplified in Fig, 3; elimination of impurities
(IC,
(e,g, oxygen, hydrogen) producing brittleness;illconversion of low-
melting eutectoidal inclusio-nZe,,_ sulphur in steels) producing
red shortness into hi:~E-melting compounds, improvement of
~resistance of s,3ale to further oxidationj change in mechan~,sm of
Plastir. deformation of the alloy base (the influence of rhenium on
the deformability,joftIL-in ~sten~Xjis shown in Fig, 7); increased
recr,ystallization tem-oerature '(the effect of various elements on
that. of moly)dena~l_ a shown in Fig~ 9) - strengthening action
through alloying of solid solution or fu.vuLation of new heat-
resis-11-a-ing compounds, or their redistribution, JIM heat treatment
ca-d. 2/3.

S/180/60/000/005/004/033
E11I/E135
Rare Metals in Heat-Resisting Alloys
(F-ig,, 11 shows the effect of s 11 dditions of,cerium on'the
atil
strength of titanium alloys) dFpar ng of special properties
toalloys, The author conclua s from this survey that rare
metals are needed for high-teaperature alloys and urges wider
arid more profound -research work in this field.
,.There are 12 figures, 7 tables and 51 references: 42 Soviet
L1Y1
(several Are t-ranslations from English), and 9 English.
SUBMITTEb- Apri-I 25, 1960
Card 3/3

82219
S/031/60/000/006/002/004
AUTHORSi Savitskiy, Ye.M.; Duysemaliyev, U.K.
TITLEt 'The Effect of,Vanadium-in the Properties of Industrial Nickel-
Base Alloys
PERIODICAL: Vestnik akademii nauk Kazakhakoy SSR, 1960, No.. 6, PP- 43 47
,TEXT.- The authors describe experiments carried out to qetermine the
effect of vanadium on structure and properties of Monel metalyand constant-
an. The alloys were prepared at the Balkh 'ashskiy zavod po obrabotke tsvet-
nykh metallov (Balkhash Non-Ferrous Metal Working Plant) and the vanadium
was introduced in the form of a Ni + 10 V alloy. They were tested as to
microstructure, hardness, electric resistance, strength and plasticity dur-
ing stretching. The stretching tests were carried out at temperatures of
from 20 to 1,1000C. Additions of vanadium of up to 0-5~o had no effect on
,the microstructure of either the Monel metal or the constantan. Measuring
the hardness of the alloys in thedeformed and tempered phases showed that
,introduction of up to 0-5% vanadium had no efft?ct on the hardness-of the
Monel metal and slightly increased the hardness of the constantan. The va-
~Card 1/2
--- -------