SCIENTIFIC ABSTRACT KORNILOV, I. I. - KORNILOV, I.I.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000824720008-0
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: June 14, 2000
• Sequence Number: 8
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

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AUTHORS: N. T. SOV/2()-12o-2-23/63
Kornilov, I. I.
Domotenko
,
,
TITLE: The Influen~ceof the AtOM:LC Concentration of Chromium,
Molybdenum and Tungsten Upon the Properties of Solid
Nickel Solutions
(Vliyaniye atomnoy kontseiatratsii khroma, molibdena. i
vollframa na svoystva tve:rdykh rastvorov nikelya)
PERIODICAL: Doklady 1kademii Nauk SSSR, 1958, Vol. 12o, Nr 2,
PP. 311-313 (USSR)
ABSTRACT: The three above,..mentioned elements of group VI of the pe-
riodic system have a body-centered (cubic) lattice and
form limited solid solutions with nickel. The solubility
of these elements decreasez from chromium in the direction
of molybdenum and tungsten,. The differences of the atomic
diameters as compared to those of nickel and their maximum
solubility in nickel are given. The replacement of the
atoms of the metal solvent by atoms of th.e dissolved sub-
stance causes additional chemical bindings in the system
which strengthen the lattice of the metal solvent (Refe-
Card 1/5 rence 1). This different solubility and the atomic struc-

The Influence of the Atomic Concentraticn of SOV[20-12o-2-23/63
Chromium, Molybdenum and Tungsten Upon the Properties
of Solid Ifickel Solutions
ture must also exert a different influence upon solid
nickel solutions. The authors wanted to determine the
rules governing these changes of property. For this pur-
pose they employed the methods of physical-chemical ana-
lysis. The measurements of the lattice period of the so-
lid nickel solution show that at equal atomic concentra-
t.ions the degree of distortion of the crystalline lattice
in nickel increases with the transition from Cr to Mo and
V1. This rule corresponds to the successive position of
these elements in the periodic system of elements and is
a consequence of the difference of their atomic diameters
as compared to that of nickel (table 1). As is to be seen
from it the greatest difference in the lattice parameters
occurs in the cases of sol.id nickel solutions with tung-
sten (W 4,6 and lo%) and the smallest difference in cases
with chromium (at the samo concentrations of Cr). Molyb-
denum takes an intermediate position. The investigation
of the specific electric resistance at the same atomic
Card 2/ 5 concentrations of Cr, Mo and W showed the sequence of the

Thb-Influonce of the Atomic Concentration of '30V/ 20-120-2-2'~-/63
Chromium, LIolybdenuiill "ad Tungsten Upon the
Properties of jolid Ifickel Solutions
increase also in this physical constant on transition from
chromium to molybdenum and further to tungsten. The soli-
dity was studied in alloys -iith 4,6 and 10d' Or, .Io and '.4
at rocil tcmperaturu, at 800 and 10000 (table 2), the heut
resistance at 600 0 and a tension of 4 kf"/MM 2 1 _3 well as at
0 2
1000 and a tension of 2 kg/min . From table 2 follova
that the ultimate-stress values at equal atomic concentrations
increase from chromium to tungsten and from tun,-sten to
molybdenum. Molybdenum yields the highest increase in
hardness of the solid nickel solutions. Thus the sequence
of influences of Cr, Mo and W in this respect does not
correspond to their position in the periodic systeiii. The
same holds for the heat resistance (determined by the method
of bendine). The corresponding curve3 at 800 and 10000 are
shown by figure .1. From this follows tli~-.t the incr.~!&se in
concentratio.i of Cr, Mo and ""' leads to the stren~;thenin6
of the alloys at the isotherm"l lines given in thu
Curd 3/5 The results of inve3ti;Sation wore gories--alizud in a joint

The Influence of the Atonic Concentration of SOVI 20-120-2-23/63
Chromium., Molybdenum and Tun,,~sten Upon the
Properties of Solid Nickel Solutions
diagram.. Fro-a this follows that the beat resistance of
the solid solutions of Cr, bio and d at all concentrations
changes in the same order as the hardness at the sL-.Lme tem-
perature. This yields un ordert A different
influence of molybdenum and. tungaten upon the electrie re-
3istance and upon the chanEe of the period of the cryatul-
line lattice of the solid solution on the one hand and
upon the hardness and heat resistunce on the other hand
can be explainud by the fact that the chemical forces of
binding decisively influence the mechanical propertied;,
An individual influence of the elements upon the chemical
strengthening of solid nickel solutions takes place here.
There are 2 fLguros, 2 tables and 3 Savlet references.
ASSOCIATIONt Voyenno-vozdushnaya inzhenernaya ukademiyu im. 11~ Ye.
Zhukovskogo (Military Aviation Engineering Acade;ny imeni
N. Yo. Zhukovskiy)
Card 4/5

v
18(4,7);25(l)
Akademiya xiauk SSSR.
PHASEJ BOOKEXPLOITATION SOV/2568
Institut nauchno--beldmicheskoy informatsii
Metallurglya I met~allovedeniye; khtmiya, metallovedeniye I obrabotka
titana (Metallurgy iand Metallogra~hy; Chemistry, Metallography,
.and Treatment'k,of Titanium),Mosoow, Iza,vo AN SSSR, 1959. 383 P.
(Se:ries: Itogi nauki; takhnicheskiye,,nauki, 2) Errata slip in-
serted. 2,700 copies printed.
Ed.: N. V. Ageyevi Corresponding Member, Academy of Sciences, USSR1
Ed- of Publishing House: V. S. Rzheznikov;'Tech. Ed.: Yu. V. Rylina.
PURPOSE:, This collection of' articles is intended for metallurgists
working with,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 .
zhurna~y for chemistry'and,metallurgy1from 1953 to 1955- For the
most part the articles are based on Y~Ion-Soviet material. No person-
alities are mentioned. References follow each article.
Card 116

KCRNILOV, L I.
Machan1cal Properties of Intftwtanic CompourAs of Iron MA Nickel."
report Presented at tbO BlOctrOcbmlcal 80clOtY M66ting, Philadelphia, 3-7 M&Y 59
Eval. B-3,1310204

PHASE I BOOK EDWITATION SOV/3559
A-kademiya nauk SSSR. Institut zetallurgii. Nauehnyy sovet po problems zharo-
prochnykh splivoy
7lasledovaniyi po zharoprochnys splaift, t- 5 (Investigations of Heat-Resistant
Alloys, Vol 5) Moscow, Izd-vo'AN SSSR, 1959o 423 P- Errata slip inserted.
copies printed.
Ed, of Publishing House: V4A. Klimoyj Tech. Ed#.- I.F. Kuziminj Editorial
Board: I.Pa Bardin, AcadeMcisn, G.V. Xurdmor, Academician, N.V. Ageyev,
Correspotiding Member., USSR Academy of Sciences (Reap. Ed.), I.A. Oding,
I.M0 Pavlovp and I.F. Win, Candidate of Technical Sciences,
PURPOSE: This book is intended for metallurgical engineers, research workers
in metallurgy, and may also be of interest to students of advanced'courses
inmetsllurgy~
007BRAO: This book., ccnaleting of a number 'of papers, deals with the proper-
ties of heat-resisting metals and alloys. Each of the papers is devoted to
the study of the fadtors which affe ct the properties and behavior of metals.
The effects of various.olements such as Qr., Mo, and W on the heat-resisting
properties of various alloys are studied. Deformability and workability
Card i/9

Cr
u
jig
.9 V'21a

VOL, Abram Yevgenlyevich; AG9W, N.V., red.; ABRIKOSOV, K.Kh., doktor
tekhn.nauk, red.; red.; SAVITSKIY, YeA. red.;
OSIPOV, K.A., doktor takhn.nauk, red,; GUSEVA, L.N', kahd.khiu.-
nauk, red.; KIRUWVSrAYA, M.S., kandAhime'usuk, red.; SWZW-
SKAYA, I.Yu.. red.; MURASHOVA, N.Ya.. takha.red.
(Structure and properties of binary metal systems] Stroenis i evoistva
dvoinykh metallichaskikh sistem. Pod rukovodstvom M.Ageava. Moskva,
Gos.izd-vo finiko-matem.lit-ry. Vol.l. (Physicochemical properties of
elements; nitrogen. actinium, aluminum, americium, bariung beryllium.
nd boron syste a] Fiziko-khimicheskis svoistva alementov; SisteU7
sot&4 aktirlia: pliumintia, ameritaiia, bariia, berillils, bora. 1959.
:
755 po (MIU 13:3)
1. Chlon-korrespondent AN SM (for Ageyev).
(metals) (Phase rule and equilibrium)

3oveshchasslye po eksperLssentalfavy tekhalke I matodam vysokotempirra-
turny" Lsolodovauly, 2956
Xk4sperimentalinaya tokhnika I metod &a ledovanly pri vymoselkh t*s-
gwraturakht trudy Toahzslquea and
methods or Investigation at Big Temperatures; Transactions of the
Conference an Experimental Techniques and Yothods of Investigation
at High Temperatures) Moscow, AN 333R, 1959- T89 P. (Sorless
Akademlya nauk SSSR. XnatItut astallurgil. tomissiya po flziko-
Ishlaichaskim canovan proizvodstva stall) 2,200 copies printed.
Reap. 24.: A.M. Sawarin, Corresponding Member, WSA Academy of
isienoss; . z4. or Publishing Houses A.L. Dankritser.
PMP=: This book is intended for metallurgists and metallurgical
anginears.
CCVM=s This collection of scientific papers is d1vidwd Into six
jartes 1) thermodynaniv activity and kintties or hirts-temPeraturs
processes 2) constitution diagram studies 3) physical properties
=tZ'- Z-A_
. _ SIMV 4) r_~W W" lvtlasl methods and pro-
ametion Of pure metals 5) pyro"try, aisd 6) general questions.
.-For sort specific coverage, 6*0 Table of Contents.
n. consTrm.Tair DIAaR&K S==S
ov. I.I. Methods or Studying NultlcOMPOtwnt Iran-Bamst
?be author bases his method an an ovwrall study of the
obealcal reactivity of the ellnedsitS Us the periodic table
i SIN "lation to a given element (in this case, 11*0n),
gpgolfleally, their ability to form solid solutions with
U-0n. go gives methods for constructing cons'-Uution
dug-" of ons2t1cosponont lron-bese alloys (5-8 components).
Sellasu, P.7m. 3tudles of Constitution DLagr&IKS Of SyStanS Of
no iterractory Wdoe IT2
A range or compositionx forming solbd solutions when heated
a found for thir followings . 0 Z? 2- blnpry mlxt
me . . 39. . V~03
(902ld-folution WISULng POIntbg 2-200r-25 C) 2) ZrQ2
to mixtures (solid-solution maltlng pointst 2200-26250C),
:rrj W-Cr,0j-Znjr.5, mixtures (solld-solutlon.
galtIMA pointes 200- 000 C Roentgenametria analysis
eatablished the formation of torns" solid solutions of cubic
modification in the range of ternary alltures of the system
zr02_ft0-Ca0. rich In zLreonlum-from 80 to 95 NOI. percent
ar Zrq2. Malting points of these mixtures fall between 2300
and 26bOu C. The absence of a sut4ctla makes these mixtures
important refractory materials.
"lakhov, P.Ta. Xlerefurnace for gardening at Tewpersturess
up to 25WO C, 184
"nakiy. T&.1. (Deceased). Investigation of HLgh-toupera-
S. Squl2lbria by the FAIIIAS-Gramula Method IST

MDRNIIOV. I.I.- BUDIMRG. P.B.
Constitutional diagrams of titanLaw-base nvatow. Itogi nanki.-
ne.2:31-102 159. (MIRA IL2.9)
(Titanium alloys) (Phase rule and equilibrium)

67294
1/2. Wo
sov/18o-59-4-31/46
AUTHOR: Kornilov. I.I. (Moscow)
TITLE: Several Problems of the Theory of High Temperature
Strength and the Development of New High-Strength
Titanium Alloystj
.1
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya I toplivo, 1959, Nr 4, pp 190-199 kUSSR)
O
ABSTRACT: The physico-chemical'basis of high temperatur
Strength
of alloys is discussed and the various methods of
measuring high temperature resistance are compared.
Fig 1 shows apparatus for measuring the strength of
alloys at elevated temperatures by the centrifugal method.
The author considers that the time to reach a given degree
of deformation by this method gives a good measure of the
strength at high temperatureq. Studies of the high
temperature strength of different types of alloy system
are described and reasons for strengthening put forward.
Fig 4 and 5 show the effectsof varying the composition of
the Au-Ag system and of the Cu-Ni systeti, at 3000C and
900% respectively. It is shown that the strength of
continuous solid solutions is retained at much highe.-
Card 1/3 temperatures than had been previously supposed. The high

~67294
SOV/180-59-4-31/48
Several Problems of the Theoryof High Temperature Strength and the
Development of New High-Strength Titanium Alloys
temperature strengths of systems with limiting solid
solution are given in Fig 7 (Ni-Zr, curve 1; Ni-Nbj
curve 2, Ni-Mo, curve 3) at 8oo*C; Fig 8 (W-.Ni, curve 1;
Ti-Ni, curve 2i Fe-Ni, curve 3i Co-Niq curve 4) at
700*C and for Ni-Cr alloys in Fig 9 and Ni-41o alloys in
Fig 10. It is shown that the strength at high temperatures
increases with the concentration of the soluble element
and renches a maximum at, the tilran8ition from solid
solution completely saturated -to haterogencous structures
with a finely dispersed precip1tate of second phase.
Results on studies of the high temperature strength by
formation of metallic compounds are given in Fig 11.
This compares the rate of creep of solid solutions of
Ni-10%Nb and Ni.-7.5%Ta (curve 1) with compounds
Ni3Ti (curve 2), Ni3Ta (curve -5), N'3Nb (curve Ik)at 1030%.
It is shown that metallic compounds have a much higher
strength at high temperature than the elements from which
they were.formed or solid solutions of the elements.
Results of heterogeneous systents of alloys with very small
Card 2/3 ranges of solid solution and no interaction between the ~K

67294
SOV/180-59-4-31/48
Several Problems of the Theory of High Temperature Strength and the
Development of New High-Strength Titanium Alloys
phases are given in Fig 12 (CuZr) and Fig 13 (NiZr).
It is shown that the strength at high temperature depends
upon the strength of the individual phases. It changes
linearly with the ratio of the phases in the system.
There are 14 figures and 40 references, 38 of which are
Soviet, 1 English and 1 German.
SUBMITTED: May 4, 1959
Card 3/3

6763b
SOV/180-59-6-14/31
AU THORS: Pi To I ing-bual and K6r&,Uav,. -1. 1.,_ (Mo s cow)
TITLE: The Constitutional Diagram of t" TiFe2-05ystem
PERIODICAL: Izzvestiya Akademii nauk SSSR20tdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo.1959,Nr 6, pp 110,112 WSSR)
ABSTRACT: The object of the present investigation was to study by
means of thermal analysis, metallographic examination,:,/--
and hardness measurements) those alloys of the ternary
Ti-Fe_'V system that lie on the TiFe2-V line. The
experimental alloys were prepared from carbon-reduced
vanadium, magnesium-reduced titanium and Armao iron,
the two latter metals having been used to prepare (in
an electric are furnace) a mastor alloy of the
composition corresponding to TiFe2 whose actual
titanium content was 29.29%. This master alloy was
then used for the preparation of the experimental
samples, made by the powder metallurgy methods,
specimens used for the determination of~ the solidus
having been made by melting in an argon arc furnace.
Card The results of the thermal analysis are tabulated on
1/3 p 110, where the vanadium content (wt-% and atom-P and
the solidus temperature (0C) of several alloys are given.~

67836
SOV/180-59-6-14/31
The Constitutional Diagram of the TiFe24 System
Fig 1 shows the constitutional diagram of the TiFep-V
systamv constructed on the basis of these data (wt-%J
bottom scale; atom-%, upper scale). It will be seen
that the melting points of both TiFe2 and V were
lowered by the addition of the other component, and that
the two components form a eutectic, melting at approxi-
mately 1400 OC. The metallographic examination was
carried out on specimens subjected to the following heat
treatments: 1) homogenization followed by annealing at
progressively lower temperatures (1000, 800 600 and 5500C
for 50, 250, 300 and 400 hours respectivelyJ and cooling
in the furnace to room temperature; 2) water-quenching
after holding at 12002 lOoO7 800 or 600 OC for 10, 2502
300 and 500 hours, respectively. The metallographic
specimens were etched in a 1:1:3 mixture of hydrochloric
acid, nitric acid and glycerol. It was found that
alloys containing up to 10% V constituted TiFei-rich solid
solutions (the micros trua ture of an alloy contiiining
Card 5% Ir �s shown in Fig 2a) . The alloys in the 10-90% V
2/3 range consisted of two phases, the alloy of the eutectic
composition containing 32% V. The microstructure

O'KA,
SOV/180-59-6-14/31
The Constitutional Diagram of the TiFe2'-V SYStOm
of a nearly eutectic alloy, containing 35,06 V7 is shown
in Fig 26; Figs 2Aand Z show oticros true t-ire of alloys
containing 60 arad 90,j~o' V, respectively, with a corres-
pondingly smaller proportion of the eutectic. Similar
structures were observed in quenched specimens~ whose
examination showed that the solid mis3ibility gap
narrowed slightly at high temperatures (see Fig 1).
The results of Brinell hardness measurements, carried
out under the load of 10 k 9 are reproduced in Fig 3
where hardness (Hv, kglmm2~ is plotted against the
composition of the alloy (wt..%) for specimens annealed
(open circles) and quenched from 1100 OG (filled circles).
Hardness of the quenched alloys was slightly lower than
that of the annealed specimens; howeverg the concentra-
tion dependence of HV was similar in both casesq the
hardn6ss curve passing through a maximum at a
concentration corresponding to the eutectic composition
(approximately 32% V). The obtained results con-firmed
Card the pseudo-binary character of the TiFe2-V system.
3/3 There are 3 figures, 1 table and 6 references, of which
2 are Soviet and 1+ English.
SUBMITTEDS May 29, 1959

5 (2)
AUTHORSs Kornilovp I. I., Kantorovioh, L. Ye. SOV/62-59 6-2/36
TITLE: Investigation of One Part of the Four-component System Fe-Cr-Ni-Mn
(Iseledovaniye chasti chetirernoy sistenq Fe-Cr-Ni-Mn)
PERIODICAL: lavestiya Akademii nauk SS.I)RO Otdeleniye khimicheskikh nauk,
1959t Br 6j pp 963-970 (USSR)
ABSTRACT: The phase diagram of the four-component system mentioned in the
title is investigated in one section (I) (Fig 3) on the line with
constant Ni-content of 10 %, parallel to the Fe-Ur part. Alloys
were inveatigated with var:'Lable content of Cr in 6 sections and
ft (Cr 10, 20, 30, 50v 60 iind 75 j;, and a change of the Mn-
content at each of these values in the range of from 0-70 %).
Armoo iron, metallic chromium, and electrolyticallyproduced
nickel and manganese were.-the components of the alloys. The
chemical composition of the alloys Iinvestigated is given in.tablel
(Table 2 contains data on their microstructure). With the ,
41loys the microstructure, the strength, the electric resietance,
and with some, also their imgnetie properties were investigated.
The data obtained by these investigations served for constructing
the diagram of the system. In the iron corner of this diagram
Card 1/2 the boundaries of the phase ranges o(,cL + jr q- and 17, and that of

.Investigation of one Part of the Four-component System SOV/62-59-6-2/36
Fe-Cr-Ni-Mn
a number of interlaying ranges were determined. Furthermore, the
dependence of the change in strength and electrical con-
ductivity on the composition and the phase construction was
investigated. Alloys with a composition of 49.7 % mn, 38 ~ Cr,
5 % Nit 7.3-% iron exhibited the highest ohmic resistance
(1.31 St/ him:'). in the system investigated 15 different phase
ranges wete determined. The most important share in the phase
diagram is held by the solid austenite (r) solution with
manganese. The phase ranges and (rdenote:4tsolid solution,
o(-Fe on Pe-basis (ferrite), and otcr on Cr-basis, the solid
ablution 2--Fe (austenite), 6-the phase of the compound FeCkt
oG&Mn the solid solution on,96Mn-basis. There are 12 figurest
3 tables, and 9 references, 6 of which are Soviet.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
*stitute'of Metallurgy imeni A. A. Baykov of the Academy of
Sciences, USSR)
SUBMITTED: September 13P 1957
Card 2/2

5(o)
AUTHOR: Kornilov, I.I. SOV/62-59-7-1/38
TITLE: Investigation.in the Field of bletallochemistry (Issledo-
vaniya, v oblasti metallokhimii) Communication 2.
The Interaction of Iron and Different Chemical Elements
(Boobahcheniye 2. Vzaimodeystviye zheleza s razl' iclrajmi khimi-
cheskimi, elementami)
PERIODICAL; Izvestiya Akademii nauk SSSR* Otdeleniye khimicheskikh nauk,
1959,Nr 7, pp 1147 - 1153 (USSR)
ABSTRACT: In this paper the problem mentioned in the title is considered
from a general point of view on the basis of data available
in publications.The different types of interaction (ionic
and metallic interaction) of iron with other elements ate
determined from the standpoint of the position of these
elements in the periodic system. The following rules are
given: the metallic analogues being similar in their electron
configuration of that of iron (situated in the proximity
of iron in the periodic system) are predominantly
capable of forming solid solutions. The elements with a d-,Lf-
Card 1/3 ferent dectron configuration tend to form chemical compounds.

Investigation in the Field of Ile tallochemis try. Comainication 2. 3UV/b2-59-'j-1/5rj
Interaction of Iron and Different Chemical Elements
In the solid solutions the two crystalline variations d0and
jr (the ferrites and austenites) were found. Iron forms
ferrites with the nearest related elements chromium and
vanadium. Austenite is always a homogeneous solid solution,
and is formed by iron with the near related elements
of the VIII group. A great number of elements (Be of the
II group, BP Al (Se) of the III group, all elements of the IV,
some of the V and VI group) forms limited solid solutions. Also elements
with small atomic radius as If, C, and 11 belong to them.
The elements 0, S and the halogens form only covalent or.
ionic bounds. The alkali metals and some heavy metals ,
(Ag, Cd, Rg, Te, Pb and Bi) cannot at all form compounds
with iron, and the same applies to all rare gases#
9 elements belong to the first group, 56 to the second,
10 to the third and 24 to the fourth. For an investigation
of the interaction in multicomponent alloys and solid
solutions the possible maximum number of components was
equated 56 + 9 = 64 + iron = 65- Since of these elements
some form homogeneous solid solutions, and the others
Card 213 only limited solid solutions, the number and the limit

Investigations in the Field of Me tall ochemi a try. Uommurdmthn 2. WV/62-59-7-1/38
Interaction of Iron and Different Chemical Elements
concentration of the elements can be determined which go into
the composition of the unsaturated solid solutions at a certain
combination of the elements. Next, the case of a 10-component
solid solution is thoroughly discussed in which the elements
forming ferrite and austenite are taking part (Ni, Pe, goo W,
Ta, Cr, Nbo Vp Ti). The possible equilibria between solid
and liquid solutions (alloy) and the possibility of a
synthesis of these alloys are dealt with. In figure 2 and 3
theol--phase and'the-r-phase of this 10-component system are
represented* There are 3 figures and 14 references, 13 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: September 13, 1957
Card 3/3

5(2), ISM SOV/78-4-7-26/44,
AUTHORS: Kornilov, I. I., Vlasov, IT. S.
TITLE., The Phase Diagram of the System Titanium - Vanadium - liobium
(Diagramma sostoyaniya sistemy titaA - vanadiv - niobiy)
PERIODICAL: Zhurnal neorganicheskoy khimii, 1959, Vol-4, Nr 7,
pp 1630-;-1637 (USSR)
A.BSTRACT: In a previous paper (Ref 12) the authors stated that all alloys
of the system mentioned in the title crystallize as continuous
solid solutions.on the basis of P-titunium. This is explained
by the small differences in the atomic diameters (Table 1) of
those element& and b the iaomorphism of the lattices of V and
Nb with that of P-titanium. The prosent paper reports about
the experimental investigation of the phase diagram and the
phas transformations in the ternary system mentioned by means
of microstructural-analysis, measurement of hardness, thermal
expansionp*and-of,.the-electric resistance. The composition of
the alloys investigated is shown by table 2 and figure 1.
Figure 2 shows pi*ctures of some microstructures, figures 3-6
show theAsothermal cross sections of the system at 10000~
Card 1/2 8000, 7000 and 6000. Figure 7 is a spatial representation

SOV/78-4-7-28/44
The FhaBe Diagram of the System. Titanium -, Vanadium - Niobium
of the phase.diagram. The upper part has the continuous charac-
ter of the solidua surface. At 8850 a closely limited range
of the solid a-solution is formed.in the titanium corner on
the.basis of the hexagonal-a-modification of titanium. Between
this range and the P-solution there is a biphase a+P-range.
There are 7 figures, 2 tables, and 12 references, 9 of which
are Soviet.
SUBMITTED: April 2, 1958
Card 2/2

5(2)
AUTHORS: Kornilov, I.I., Nints, R. S, SOV/78-4-9-39/44
TITLE: A Nickel-aluminum Alloy With a Low Linear Expansion Coefficient
PERIODICAL: Zhurnal neorganicheskoy khimii, 1959F Vol 49 Nr 9t pp 2169-2171
(USSR)
ABSTRACT: In connection with the investigation of the phase diagram of the
ternary system Ni - Cr - NiAl (Refs 1-4) an alloy with a low
expansion coefficient was found in the system Ni - Al . In order
to determine the composition of this alloy the hardness (Fig 1)v
microstructure, electric conductivity and its temperature
coefficient (Fig 2), as well as the linear expansion coefficient
(Fig 3) wer3 determined for different Ni-Al alloys. The results
showed that the alloy with the lowest linear expansion
coefficient corresponds to the compound Ni Al. There'are
. 3
3 figures and 8 references, 6 of which are Soviet.
SUBMITTED: January 12g 1959
Card 1/1

5(2)
"AUTHORS: Boriskina, N. G.v Kornilov, 1. 1. SOV/78-4-9-40/44
TITLEz A Ternary Metal Compound in the System Iron - Chromium -
Titanium
PERIODICAL: Zhurnal neorganicheskoy khimii, 1959, Vol 4, Nr 99 PP 2171-2173
(USSR)
ABSTRACTs On the occasion of the investigation of the phase diagram of the
ternary system Fe - Or - Ti the authors investigated the alloys
in the cross section TiFe2 - recr (d -phase). The alloys were
prepared by melting in an electric arc in an argon atmosphere.
By means of a microstructure analy is it was found that the alloy
consisting of 15.7 atom% Tit 25.8 :tom% Or, and 58.5 atoni% Fe is
a single-phase alloy and hiejaly brittle in a cast state. By
tempering at.10000 the alloy is decomposedt andfinely-dispersed
needles develop which form a definite angle with the ground
surface (WidmannstAtten texture). The radiographs of this alloy
were taken for the cast and tempered state (Table 1, Fig i).
The lattice constant corresponds to that phase which was found
Card 1/2 in the system Fe - Cr - No (Ref 3) and later in alloys of

A.Ternary Metal Compound in t?Ae System BOV/78-4-9-40/44
iron - Chromium - Titanium
binary and ternary systems (Refs 4-6) and which is called the
X -phase. In the system Fe - Or - Tit therefore, such a phase
would also form. Its composition aorresponds to the formula
Ti5Or7Fe 17' It d*coaposes at 10000 and forms the Laves phase
TiFe 2' Thus it Is, in factv a transitional stage between the
Laves phase and C'-phase. Thero are 1 figurep I table, and
6 references, 2 of which are Soviet.
SUBMITTED: April 60 1959
Card 2/2

S 0 V/ 1. 6
AUTHOR15: KorrJJ.I.OV. -r.l., Pylaft~va, and Volh-ctru, M.A.
TITLE: Inveixtigation of the Prepwtio-.- of TitAY0.-ant A,Ll;)y2,,
IV. Prap,,ortias of Alloyt or 'h~:t Torvnrv Sy0tQ,11
PERIODICAL: Flzika metall-zv -I :1.959t V"n-11 6, Nr 2,
PP 182 - 1846 (USSR)
ABSTRACT: The toriiary-phaiza dlag,=am tAt 550 c'c; i~~ givp-a in Figure 1.
Sample6 co~~trdnlnA '-up t,.) 20% were prapa-r;~d-'. by
powder rx o tho d The high trmpora-~~u--e
5trength was te-z%tz~d T,y f-lm- xlsirv~ a
stres:~- 0:v 15 kg/run2at-, ~550 t-* 7c0, -1~ C.
The change iii th;~., oi7 -up tc 1.00 bo'v--rz, fo.-V
varic-us alloyo :L,-; giir~-';a kyi Fr(;m rals I t
b-- se-3n tha~t urit-diu-,un ilF
by twe-phazz~ alloy;.4 ((.*--arva~s I aad 1). Thp- U-Tvc-
of an a-lloy contaixAng 34.75~'G' Al and 11-23%j Fe Is 'r cl: A
in Figure 3. Thu ligHt cnorst-itu--oJ7 is -:1 e-mift
the dark `16;~,- CIL eutcctuid of a-,--Tj-FE. 1,he b1gh-temper,.iture
strength of r-lloys ccntrJ.ring, Fe 4rL--,l Al in tho ratii~, 1:1.
Th;, mic~r-r-tructure, nf an
is great"r (C-UrV115 3 axd
Cardl/3

SOV/126-8-2-5/26
Investigation of the Properties of Titanium Alloys. IV. Propertiem
of Alloys of the Ternary Ti-Al.-Fe System
alloy containing 6.50% Al and 6.50% Fe is- given in Figure
The high-temperature strength of ternary alloys containing
3-75% Al and 1-25% Fe is even greater. The microstructure
of such an alloy is shown in Figure 5. It consists Pf solid
solution with a small amount of eutectoid in the grain
boundaries. The greatest high-temperature strength is shown
by alloys containing 0-5% Fe and 1-8% Al (Curves 7 and 8).
These alloys correspond to the limiting region of transition
to a two-phase structure. CurveB of high-temperature
strength against time are given in Figure 6. These show
that pure T! has the least strength and. an alloy coutaining
7.5--8% Al and 0.5% Fe has the greatest strength. Figure 7
shows the mdcrostructure of this alloy after test. It
consists of solid solution with a finely dispersed pWasa.'
As in binary TI-Al alloys, increase in Al content leads to
increase in str*ength but decrease in plasticity.
Increasing the Fe content to greater than 0.5% causes a,
Card2/3 decrease in high-temperature strength.

Is sov/i26-6-2-5/26
. Investigatlon of the Proper-ties of Titanium Alloys. IV. Properties
of Alloys of the Ternary Ti-Al.-Fe System
There are 8 figures and 13 Soviet referencez.
ASSOCIATION: Institut metallurgii
(Inmitlat* of Metaal=%Y' imeni Baykov)
SUBMITTED: Marzh 95, 1958
Card 3/3

66225
SOV/126-8-3-8/33
AUTHORS: Kornilov, I.~., Qlazunov, S.13'. and Yakimova, A.K.
TITLE: Influence of Hydrogen on the Properties of a Higher
Creep Llmit VT-8 Alloy
PERIODICAL: Fizika metallov i metallovedeniye, 1959, Vol 8, Nr 39
pp 370-377 (USSR)
ABSTRACT: The present paper is a continuation of a series of
papers dealing with the study of the influence of
hydrogen.on the properties of commercial titanium alloys
of a + p-structure. The aim of the present investigation
was to study the influence of different hydrogen contents
on the properties of the VT-8 alloy (residual deformation
not more than 0.2% after 100 hours at a stress of
24 kg/mm2 at 500*0. The following melts of the VT-8
alloy were studied: (1) melt 7: 6.35; Al, 2.9% Mo.
0.12% Fe, 0.08%.Sig 0.1% 0,, at the following hydrogen
contents: 0,005, 0.015, 0.025, 0.05 and 0.08%;
(2) melt 8: 6-3% Al, 3.25% Mo, 0.20% Fe, 0.070,,i Si and
0.2% 02 at the same hydrogen contents; (3) melt 10-1:
6.6% Al, 3.0% No, 0.05% Fe, 0.04% Si and 0.1j4 02 at
the following hydrogen contents: 0.005, 0.015, 0.025%;
(4) melt 10-3: 6.6*j'Q Al, 3.0% Mo, 0.05% Fe, 0-04% Si
Card 1/6 and 0.3% 02 at the same hydrogen content as (3).

66225
SOV/126-8-3-8/33
Influence of Hydrogen on the Properties of a Higher Creep Limit
VT-8 Alloy
Th* alloys were saturated with hydrogen in a specially
constructed universal instrument for the saturation of
metals with games and for the analysis of hydrogen.
Extremely pure hydrogen was obtained by thermal
dissociation of titanium hydride; the saturation
temperature was 700%. Melts of the VT-8 alloy with
different oxygen contents were obtained by alloying with
titanium dioxide. An identical initial state of the
billets after saturation was ensured by subsequent heat
treatment which was carried out in electric furnaces in
air atmosphere. The heat treatment of the VT-8 alloy
consisted in annealing at 8e06G for 1 hour, followed by
cooling in air. The mechanical properties were
investigated by using (iagarin-type specimens at a
straining rate of 2.5 mmlmirt (Fig 1). The properties,
were investigated of specimens in the original condition
(88o*c - I hour)* of specimons aged at 5000C for IOU houre
and specimens aged under a stress a = 10 kg/mm2 at 500'c
for 100 hours. The UTS was found to have increased after
Card 2/6 ageing from 112 to 125 kg/=a2 and to have changed littl
66225
SOV/126-8-3-8/33
Anfluence of Hydrogen on the Properties of a Higher Creel) Limit
VT-8 Alloy
with increase in hydrogen content. Fig 2 shows the
dependence of the mechanical properties of the VT-b alloy
on the hydrogen content and the rate of testing. (Ful.1
lines - annealed at 8800C for 1 hour: dashed lizies. -
annealed at 80*C for 1 hour followed by 500 0C f or 100 houris,)
Fig 3 shows the dependence of impact resit-3tance of tite
VT-8 alloy on the hydrogen content and Vie testing
temperature. Metallographic investigation of the VT-8
alloy with various hydrogon contatits iirijs c(irl-ic(I
At room temperature, the alloy has a two-litio6o a +
A-structure. The effect of hydro,-ren oii the structure of
the alloy consists in coarsening the structural compunenLs
as the hydrogen content increases (Fig 01 aild 5) alid
apparently also in increasing the quantity of' untransforuied
P-phase. Fig 6 and 7 show flie results of telisile tet3tilig
of two, VT-8 alloys containing 0.1 and 0.3% oxv1sorl,
respectively, in relation to the hydrogen content.
Fig 8 and 9 show photomicrographs of two VT-8 alloys with
an oxygen content of 0.1 and 0.354' and different hydrogen
Card 3/6 contents. An investigation of the influence of hyd

66225
SOV/126-8-3-8/33
Influence of Hydrogen on the Properties of a Higher Creep Limit
VT-8 Alloy
on the creep of,the alloy VT-8 was carried out.
Two VT-8 alloys of 0.1 and 0.2% oxygen and 0.005,
0.015 and 0.025% hydrogen were investigated for creep 2
properties at,5000C.after 100 hours at a stress of 10 kg/mm.
As the hydrogen content increased from 0.005 to 0.025 an
increase in the residual deformation was observed (see
Table 1). The influence of hydrogen on the stabilization
of the residual ~-phase in the VT-8 alloy Under various
heat treatments is shown in Table 2. The authors arrive
at the following conclusions: (1) Investigation of the
influence of hydrogen within the limits 0.005 and 0.05%
on the mechanical properticia of the VT-8 alloy has shown
that a considerable lowering of plastic properties occurs
at a hydrogen content of 0,015% which is associated with
the instability of the A-phase in the structure and its
decomposition. (2) The investigation of the influence of
hydrogen on the properties of the above alloy at various
straining rates has shown that the plasticity of the alloy
decreases considerably at low testing rates, particularly
Card 4/6 when the hydrogen content is increased. The UTS of the

66225
SOV/126-8-3-8/33
Influence of Hydrogen on the Properties of a Higher Creep Limit
VT-8 Alloy
alloy increases from log to 117 kg/mm2 on increasing the
testing rate from 0-17 to 48..2 mm/min respectively (at a
hydrogen content of 0.005%). (3) The impact resistance
of the alloy at room tempera-Lure and sub-zero temperatures
(-78 to -196*c) changes relatively little in the hydrogen
content range of 0.003 to 0.08~0'. The testing
temperature exerts a considerably greater influence than
the hydrogen content up to 0.08%. (4) As the oxygen
content increases, the hydrogen exerts an ever increasing
unfavourable influence on the properties of the alloy,
(5) In the investigation of the influence of hydrogen on
the creep of the alloy at 50D*C in 100 hours, it has been
found that as the hydrogen content increases, the extent
of residual deformation increases. Oxygen increases the
creep resistance of the alloy. (6) The phase analysis
of VT-8 alloys with different hydrogen contents has
confirmed the presence of residual P-phase in the structure.
At low hydrogen contents (UP to 0.015100 the residual
P-phase is unstable and during ageing a redistribution of
Card 5/6 molybdenum between the a and P-phases takes place. As the

66225
SOV/126-8-3-8/33
Influence of Hydrogen on the Properties of a Higher Creep Limit
.VT-8 Alloy
hydrogen content-increases, the O-phase becomes stable
and its unit cell parameter increases. There are
9 figures, 2 tables and 9 ref4trences, 2 of which are
Soviet and 7 English.
SUBMITTEDs June 21, 1958
Card 6/6

5 (2)
AUP HORS Kornilov, 1. 1., Vullff D. K. SOV/74-28-9-4/7

TIT1,E: TJetallic Compounds
PERIODICAL: Uspe-khi khimii:., 1959, Vol 28, Nr 9, pp 1086-1113 (USSR)
ABSTRACT: Ia the present paper the.atithors want to show by means of some
examples the wide distributioa of metallic compounds In alloys,
they also refer to the importimce of a further development of
this branch of inorganic chemistry. The paper begins with brief
historical survey'on the origin of metallic compounds (Refs 1-16).
This introduction is followed by classification and description
of the physico-chemical naturo of these compounds (Refs 10, 15,
17-42), as well as by a description of the conditions'under which
the metallic compounds are f o,.Med,- in particular in regard to
11,
their solid solutions (Refs 4., 15, 43-48), whereupon the reneral
properties of these compounds are set forth (Refs 49-55). To
give a general characteristicis of these compounds it is
recommen to subdivide them into specific groups having
certaift features in common, e.g. on the basis of similar crystal
structures, or their genetic relationship as
reflected by their conditions of origin and formation. The autbM
Card 1/4 describe certain characteristics of the origin within the frame

Metallic Compounds SOV/74-28-9-4/7
of the different groups and lay stress on the modifications of
their composition and prop'erties according to the position of
the elements within the periodic system. Such compounds are the
following: compounds according to Kurnakov (Refs 56-111),
metallic compounds with the valency correspondence to the atoms
(Refs 43, 529 112-116); electron bonds; (Refs 16, 117-121),
metal bonds of the type of the phases according to Laves (Refs 122-
126); bon'ds of the type of nlLckel-arsenic phases (Refs 127-129);
hydrides.(Refs 19, 133-137), borides (Refs "38-141), carbides
(Refs 142-152); silicides (Rofs 153-155), and nitrides (Refs 156-
159). The origin of the Kurnakov compounds is highly interesting
as the chemical interaction between the metals becomes clea7~ly
apparent. These examples cannot any more be considered as ex-
certions, but as typical, regular results of transformationsp
taking place during the 00014 of the majority of the solid
- JLng
solutions. As the authors emphasize that many alloys are gaining
in practical importance in viewof their particularhighly
valuable properties such as IL high degree of hardness,
thermal stability, chemical otability, resistance to corrosion.
This refers also to magnetic and properties (semi conductors),
Card 2/4 and the like. A step further leads us to the use of metallic

Metallic Co.-apounds
SOY/74-28-9-4/7
compounds as independent bases for the development of new
alloys. Further researches in the field of binary, ternary, and
even higher metallic compounds on the basis of the periodic
system of Mendeleyev might greatly help in revealing the
chemical nature of these compounds so as to enlarge the field
of practical use. If the researches were to bring to light
certain regularities or natural laws in certain groups,this
might permit to predict the appearance of such rules also in
still uninvestigated domains of binary, ternary, and even higher
systems. One of the most characteristic features of the metals
and the metallic compounds is their capability to form solid
solutions with one another and with other metals. Such solid
metallic s~;Iutions on the basis-of these compounds, may consist
of a great number of components. They are the chief components
in the composite multi--Compoaent metallic alloys. Thanks to this
fact it is possible to simplify substantially the analysis of
composite systems by dividing them into simple components in
which the double compounds are independent components. The
following 8-bviet authors are mentioned:,.V,. I. Mikheyevap G. B.
Bokiy, P.J. Kripyakevich, Ye. Ye. Cherkashin, N. V. Ageyev,
Card 3A Ye. S. Makarov, Ye. M. Savitskiy, A. F. Ioffe, S. To '

Metallic Compounds
SOY/74-28-9-4/7
Konobeyevskiy, D.-h. Bernal, I. S. Gayev. There are 13 figuresv
2 tablas, and 159 referencest 90'of which are Soviet.
ASSOCIATION: VOYenno-vozdushnaya inzhenernaya Akademiya im. N. Yej
Zhukovskogo (Military Academy of Aviation-engineers imeni
N. Ye. Zhukovskiy)
Card 4/4

5W
AUTHOR: Kornilovt 1. j.._~ctor of Chemical SOV/30-59-1-31/57
TITLE: News in Brief (Kratkiye soobahcheniya) Symposium on Physical
Chemistry of.Netalli.c Solutions and Compounds (simpozium
yo fizicheskoy~khimii metallicheskikh rastvorov i soyedineniy)
PERIODICAL: Vestnik Akadomii nauk SSSRp 1959p,,Nr 1, pp 116 - 119 (USSR)
ABSTRACT: The symposium took place in London, June 4-6-.. 1958
and had been called by the English tational Physical Laboratory.
Task of the symposium was the discussion of theoretical and
experimental investigations in the field of physical chemistry
of metals and alloys and the solution of practical problems.
200 representatives from 15 countries took part in the sym-
posium. Apart -from the reports by western scientists 0. Kubashev-
read a report by,'N. V. Agayev (USSR) an the
experimontal-investigation of electron density of metals and
alloys. A.-F. Kapustinskiy (USSR) discussed the electronega-
tivity of metals and some properties of metallic solutions.
1. 1. Kornilov (ISSR) regarded the form(Ltion of mixed crystals
Card 1/2 of metallic compounds from the general point of view. The

5(2)
KornilovD 1. 1.9 Kolomytae,v, P. T. SOV/20-125-2-23/64
TITLE: Continuous Solid Metallide Solutions in the Trinary System
Co-Ni-B (Nepreryvnyye metallidnyye tverdyye rastvory v
troynoy sisteme Co-Ni-B)
PERIODICAL: Doklady Akademii nauk SSSR, i9599 Vol 125, Nr 29 PP 325-326
(USSR)
ABSTRACT: The first-mentioned author (Refs 19 2) has formulated the
basic conditions of isomorphism in metal compounds on the
fulfilment of which continuous solid solutions among these
compounds can be formed-, 1) the crystal lattiops should be of
the same type; 2) the compounds participating ir the formation
must be atomically similar; 3) the types of chemical linkage
must be identical; 4) one and the same element must be contained
in the compounds; 5) the stoichiometrical composition of the
compounds must be identical, and 6) continuous solid solutions
must be formed among the metals forming the compounds. For the
above-mentioned solutioneq the author has coined the term
metallide solutions (metallidnyye rastvory) (Ref 2). Scientific
publications do not contain any investigations into the systems
Card 1/3 from lower borides with regard to the formation of the solutions

continuous Solid Metallide Solutions in tho Trinary SOV/20-125-2-23/64
System Co-Ni-B
mentione(tin the titl,3, Therefore, the authors investigated
2 metallide systemst Go3B-Ni3B and Cc 2-Ni2B. Firstq the binary
compounds Co B9 CO B; Ni B and Ni B were produced. The
3 2 3 2
investigation of the x-ray photographs of all samples showed
the alloys of the.aystem Co Ni B to be monophasic (Fig ~1).
3" 3
Their crystal latticeik,.are Isomorphous to the lattices 9f the
pure co&L)oundB Co B and-Ift . The alloys of the system
3 3
Co 2-N12 B (Fig 2) are also hostogeneous and possess tetragonal~
crystal lattices which are~ivomorphous to the lattices of
Co2B and Ni...B. Figure 1 shows the x-ray photograph of the
trinary system. The voluma of the unit cell decreases with
rising nickel content in the solid solutiono Microscopic
analysis confirmedthe formation of monophasic structures
in said systems. Figure 3 shows a microphotograph of the
system Co B-Ni B (30 and 70%). As may be seen from it, the
alloys ha4e hologeneous structures. Figure 4 shows the alloy
Card 2/3 Go2B and Ni2B with 50% contents of each of the components.

Continuous Solid Metallide Solutions in the Trinary SOV/20-.125-2-23/64
System Co-Ni-B
Measurings of micro-hardnesei showed the hardness of the
continuous solutions in the system Co 3B-Ni3B to be practically
independent of the composition of this systemg and to amount
to 1145 kg/mm2~ also with respect to the components, at a load
of 50 g. Thus the existencs of continuous metallide solid
solutions among the above-mentioned lower borides has been
established. There are 4 figurea,~ I table, and 8 references,
7 of which are Soviet.
ASSOCIATIONt Voyenno-vozdushna:ya inzhenernaya Akademiya im. I,, Te. Zhukovskojp
(Military Aviation Engineerir~fAcademy imeni N. Ye. Zhukovskiy)
PRESENTED- December 27, 19589 by I. I. Chernyayev, Academician
SUBMITTED: December 229 1958
Card 3/3

-,-AUTHOR: Kornilov, I. I. SOV/20-128--4-24/65
TITLE: Synthesis of Multicomponent Solid Titanium Solutions
PERIODICAL: Doklady Akademii nauk SSS:1, 1959, Vol 128, Nr 4, Pp 722 725
(USSR)
ABSTRACT: Most metals, particularly those with an unfilled d-electron
shell belonging to the gr3up of transition metals, tend to form
solid solutions with many elements. One of these metals is
titanium (Ref 2). Similar chemical propertiea of the crystal
lattice, and a not too large difference in atomic radii, are
necessary for the formatiDn of a solid solution. With such ele-
ments, titanium forms continuous solid solutions, whereas with
many others only limited solid solutions are formed. The rules
found by the author in previous papers (Refs 2-5) concerning
binary and ternary systems on a titanium basis make it possible
to solve th'e problem of synthesizing solid solutions with given
compositions. This is possible in the case of n components if
the respective elements form, with titanium, solid solutions of
the two types mentioned (Ref 6, example of nickel). On the basis
of the theory of metal chemistry, the author calculated the com-
Card 113 positions of solid 5--, q-, and 10-component titanium solutions,

ISynthesis of Multicomponent Solid Titanium solutions SOV/20-128-4-24/65
for the following systems:
With 5 oomponents: Ti Al - Si - Or - Fe
9 : Ti Al - Sn - Si. - V Nb - Or - Mo - Cu
10 ; Ti Zr - Al - Sn - Si V - Nb - Cr - Mo -Gu
Table I indicates some prope.~ties of the above elements, further
the concentrations calculated for synthesizing the said systems.
The present paper discusses solid solutions on the basis of
solid a-titanium solutions with hexagonal lattice. They are
produced by prolonged homogenization annealing, and slow cool-
ing of the alloys down to room temperature. The components were
melted in a vacuum arc furnace. The sample castings were forged
to 20-25% reduction, and subjected to homogenization annealing
at 1200-12500 in vacuum for 10 hours, then slowly cooled down
to 6ooo , and annealed at this temperature for 300 hours. After
cooling down to room temperature in the furnace, the alloys were
subjected to a micro- and X-ray structure analysis, and their
hardness was measured. It was found that the 5-, 9-, and 10-com-
ponent alloys synthesized on the basis of calculations corre-
spond to a nonequilibrium. solid solution of a-titanium. This'
Card 2/3 titanium is marked by a peculiar "basket" microstructure of the

synthesis of Multicomponent Solid Titanium Solutions SOV/20-128-4-.24/65
deoomposition product of the solid a-Bolution without excess
phases (Fig 1). The author did not succeed in obtaining com-
pletely homogeneous polyhedra in this procedure. The X-ray
pictures show that, in all of the 3 alloys, all additional
lines are missing, except for those corresponding to the hexa-
gonal lattice of the solid c-titanium so'utions. The lattice
periods of these solid aolutiona (measured by a precision meth-
od) show that the hexagonal lattice is maintained with an ia-
creasing number of alloying oonstituents, while the lattice
parameters ale and the ratio c/a, as well as the hardness, are
increasing. Thus, the synthenis mentioned in the title with a
given chemical composition is well possible. T. S. Chernova
investigated the alloys, A. Ya. Snetkov made the X-ray investi-
gations. There are I figure, I table, and 6 Soviet references.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk. SSSR
(Metallurgical Institute imeni A. A. Baykov of the Academy of
Sciences, USSR)
PRESENTED: May 15, 1959, by I. I. Chernyayev, Academician
SUBMITTED: May 12, 1959
Card 3/3

-V
V
PHASE I BOOK EXPLOITATION SOV/3791
Soveshchaniye
po obrabotke zharoprochnykh splavov" Moscow, 1957.
Obrabotka zharoprochnykh splavoyi [sbornik dokladov...] (Treat-
ment of Heat-Resistant Alloys; Collection of Papers Read at
the Conference).. Moscow, Izd-vo AN SSSR, 196o. 231 0. 3,500
copies printed.
Sponsoring, Agencies:. _-Akademiya nauk SISSR. Institut mashinovedeniya.
Komissiya~po tekhnologii mashinostroyeniya; Akademiya nauk S&IML
institut metallurgii im. A.A. Baykova. Nauchnyy sovet po problemam
zharoprochnykh splavov.
Respi Ed.- V.I. Dikushin, Academician,,, Ed. of Publishing House:
V.A. i;tov; 'Tech. Ed,: V.V. Bruzgull.
PURPOSE: This book is intended for metallurgists.
COVERAGE: The book consists of thlity papers read at the Conference
on the~Trsatment.of'Heat-Resistant Alloys held in Moscow by the
Committee on Machine-Building Teohnology, Institute of the
Card 1/~

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PHASE I BOOK EXTLOITATIO14 SOV/4617
Akademiya nauk SSSR. Komissiya po analiticheskoy khimii
Analiz gazov v metallakh (Analysis of Gases in Metals) Moscow, 1960. 304 P.
(Series: Its.- Trudy) tom. 10) Errata slip Inserted. 4,000 copies printed.
Sponsoring Agency: Akademiya nauk SSSR. Institut geokhimii I analiticheskoy
khimii imeni V.I. Vernadskogo. Komissiya po analiticheskoy khimii.
Resp. Ed.: A.P. Vinogradov, Academician; Ed. of Publishing House: A.L. Bankvitser;
Tech. Ed.: V.V. Bruzgult.
PURPOSE- This book is intended for laboratory personnel,concerned with gas
analysis in metals.
t
COVERAGE.- This collection of articles is based on materials of the Commission on
Analytical Chemistry AS USSR on oblems dealing with gas analysis in metals.
The articles present data on: 1 The vacuum-fusion method, developed by Euro-
pean scientists and the Soviet scientists N.P. Chizhevskiy and Yu.A. Klyachko,
for the analysis of gases in steel and aluminum, and now applicable to analysis
of gases in other metals. 2) The research of Z.M. Tu:7ovtseva and coworkers at

Analysis of Gases in Metals
507/4617
the Institute of Geochemistry and Analytical Chemistry imeni V-T. Vernadakiy
AS USSR, Moscow, making it possible to evaluate the practicability and fields
of application of the different analytical methods. 3) The contributions of
Yu.k. Klyachko and coworkers in their study of thermodynamic methods for the
evaluation of suitable conditions for carrying out analysis. 4) The deter-
mina~ion of gases in metals by the sulfurous method as developed by A.K. Bab-
ko, 5) The spectrum isotope method for the determination of hydrogen as
developed by A.N. Zaydell and coworkers. The authors of these articles eys-
tematize and review critically the various. analytical methods, describe the
apparatus used in analysis, and indicate the basic trends of research. Ref-
erences accompany most of the articles.
TABLE OF CONTENTS:
[Vinogradov, A.P.1 Foreword
I. THEORETICAL PRINCIPLES OF GjS ANALYSIS IN METALS
3
Klyachko, YU.A. [Tsentrallnyy-nauchno-iseledovatellskiy institut chernoy
metallurgii - Central Scientific Research Institute of Ferrous Metallurgy,
Moscow]. State of Gases in Metals and Methods of Determining Them 5

Analysis of Gases in Metals SOV/4617
Klyachko, Yu.A., L.L. Kunin) and Ye.M. Chistyakova [Central Scientific Re-
search Institute.of Ferrous Metallurgy, Moscow3- Physicochemical Principles
of Gas Determination in Metals by the Vacuma-Fusion Method 10
Kornilov,_I.I._ [Institut metallurgil imeni A.A. Baykova AN SSSR - Institute
31--ge-taliurgy Imeni A.A. Baykov AS USSR, Moscow]. State Diagrams of the
System of Wth Group Elements-Oxygen 17
Gel,d, P.V., and R.A. Ryabov [Uraltskiy politekhnicheskiy institut imeni
S.M. Kirova - Ural Poly-technic Institute imeni S.M. Kirov, Sverdlovsk]. Ef-
fect of Alloying Elements onthe Hydrogen Diffusion Rate in Steel at High
Temperatur6s 27
kyabov, R.A., and P.V. Gel'd [Ural Poly-technic Institute imeni S.M. Kirov,
Sverdlovsk). Effect of Phase Conversions on the Hydrogen Diffusion Rate
in Steel 37
Fedorov, S.N., L.L. Kunin, and L.M. Sachkojra [Central Scientific Research
Institute of Ferrous Metallurgy, Moscow]. Effect af the Structural Factor on
Hydrogen Diffusion in the Fe - Ni - Mn Alloy 46
6 64~a_

//00
AUTHORS: Boriskina, N.G., and
TITLE: Investigation of the
-Mhroniiu~a-Aitanium in
and Caomium
68685
EV180/60/000/01/006/027
KorrLilc:v, I.I. (Moscow)
----- 0
EJSuilibrium7D-=5rE--a-n4of Iron-
the Reg-ion of Alloys Rich in Iron
PERIODICAL- Izvestiya Akademii nauk SSSR Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivog 1~60,Nr 1, PP 50-58 (USSR)
ABSTRACT: The object of this work was t,-o elucidate the nature of
the chemical reaction of iron with chromium and titanium
and eetablish the equilibriwi diagram for iron- and
chromium-rich alloys. Although much work has been
published on Fe-Cr (surveyed in Ref 1), Fe-Ti (Refs 5-9)
and Ti-Gr (Refs 10-14), there. is little on the ternary
system, and in some of these (e.g. Ref 15) impure_
materials were used. The compositions of alloys used in
the present work are shown in Fig 1 and tabulated. They
included alloys of the TiFe2-FeCr and the TiFe2-Cr
sections, and of three sectians with constant T-1 ' : Cr
ratios 6f 3 --l, 1 : 1 and 1 : 3, and some alloys
Card along sections parallel to the Fe-Cr side with 5, 10, 15,
1/3 20 and 25% 1~i. Alloys were made from-electrolyt;ic iron
(99-901b Fe) , elec-trolytic chromium (99. 951% Or), and

686b
13/180/60/000/01/006/02?
)3111/E135
Investigation of the Equilibrium Diagram of Iron-Chromium-Titanium
in the Region of Alloys Rich In-Iron and Chromium
iodide titanium (99.8591- Ti) by are melting under argon.
The cast alloys were homogenized at 1100 0 for 100 hrs
enclosed in quartz capsules and were studied after
quenching from 1000 OC (holding time 100 hours) and
after annealing at 550 00 for 500 hours. X-ray analysis
was carried out with unfiltered vanadium radiation in a
RKU86 camera; hardness was measured with a diamond-
tipped Vickers machine, and microstructures were also
examined. Fig 2 shows miorostructures of various alloys
after different heat treatments, and Fig 3 typical X-ray
patterns for TiFe2-FeCr. The hardness of specimens of
the different constant Ti:Cr sections as functions of %
.(Ti + Cr) is shown in Fig ~. The 550 OC and 1000 OC
isothermal sections of the Fe-Cr-Ti system are shown in
Figs 5 and 6, respectively. The work showed the presence
of a compound of composition T'5 Cr?Fel? of the alpha-Ma
Card type- at high temperatures this compound forms a narrow
2/3 range of solid solutions with alpha and gamma phases
decomposing at 1000 and 550 OC. The eutectic nature has

68685
8/180/60/000/01/006/027
Elll/E135
Investigation of the Equilibrium Diagram of Iron-Chromium-Titanium
in the Region of Alloys Rich in Iron &ad Chromium
been demonstrated of crystallization in the region of
alloys adjacent to the Ti-Fe side, in TiFe2-Cr section
alloys and in & wide range of alloys on the right-hand
side of this section with a b-igher chromium content.
The range of the Fe and Cr-base ternary alloy at 1000
and 550 00 lies along the Fe--Cr side. The solubility of
Ti in the alpha-solid solution at 1000 00 increases from
the Ti-Fe side and is about 5% on the average, falling at
5500. The extents of phases at 1000 and 550 OC have
been found. The hardness was found to be greatest in
the X-phase region, which decomposes to form the
Card compound TiFe2.
3/3 There are 6 figures, 1 table and 16 references, of which
6 are Soviet, 7 English, 2 German and I Japanese.
1/
SUBMITTED: October 5, 1959

'11/180/60/000/01/011/027
1'071/913 5
AUTHORS: Kornilov, I.I., and Polyakovs:,. R.S. (Moscow)
TITLE: The KeltIng Diagram of the Tornary System
TitLnium2VjnadjjjmAM e ~num
q~
PERIODICAL:.Izvestiya Akademil nauk WERIOWeleniye tekhnicheskikh
nauk, Metallurgiya i.toplivo, 1960,Nr 1, pp 85-89 (USSR)
ABSTRACT: The melting diagram of the complete ternary system
titanium-vanadium-molybdenum was determined. As starting
materials for the preparation.of alloys, powdered metals
of the following purities were used; Ti 99.6%, V 99.2%,
and Mo 99.9%. For the determination of temperature of
the beginning of melting, specimens were prepared by the
ceramometallic method in the form of rectangles
6o x 5 x 5 mm. All alloys were sintered at 1500 OC for
50 hours which was sufficient for vanadium-rich alloys;
the remaining alloys were resintered at 1800 OC for
50 hours. For the determination of polymorphic trans-
formations of ternary alloys In solid state, 10-g
Card specimens were prepared by melting in an arc furnace
1/3 (3 times). The specimens were sealed in quartz tubes and
thermally treated by the following procedure: heating V

SI/180/60/000/01/011/o27
R()71/H13 5
The Melting Diagram of the Ternary System Titanium-Vanadium-
Molybdenum
1100 OCI soaking for 100 hoursp slow decrease of the
temperature to 800 OCt soaking for 50 hours, decrease in
temperature to 500 OCI soaking for 300 hours and cooling
with the furnace. The melting temperatures of the
alloys were determined by the method described in Ref 15.
The composition of alloys and temperatures of the
beginning of melting are givon in Table 1, polythermal
cross-sections of the system in Fig 11 the solidus
diagram of the system in Fig 2. Polymorphie
transformations of the ternary alloys in solid state were
studied by differential thermal analysis (Table 2, Fig 6).
Steady changes of,melting curves with changes in
composition of alloys indicate that they crystallise as
continuous solid solutions. Microstructural analysis
of hardened specimens confirmed unlimited solubility of
the elements in each other above the temperature of
Card polymorphic transformation of titanium. The temperature
2/3 of polymorphic transformation of ternary alloys decreases,__~
with increasing content of molybden um and vanadium in
S/180/60/000/01/011/027
9071/9135
The Melting Diagram of the Ternary Sys~tem TitaniUm-Vanaclium-
14olybdenum
basis of the data obtained7 the
SUBMITTED:
on the
the alloys. structed
equilibrium diagram of the sYstem was con
(FIg 7). 2 tables and 15 references, of
There are 7 figurOsi
which 10 are English, 3 Soviet and 2 German.
June 249 1959
Card 3/3

69660
s/18o/60/000/02/ol6/028
EMIE152
AUTHORS: Kornilov, I.I.-~ Pryakhina L.I.9 and Ryabtsev, L.A.
(NOS -coWj_====---__
TITLE: ons'
Properties of Multi-Component Nickel Solid Soluti
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
'nauk, Metallurgiya i toplivo, 1960,Nr 2, pp 110-114 (USSR)
ABSTRACT; Kornilov has already show'M (Refs 1 and 2) that the
ability of elements to form solid solutions and inter-
metallic compounds with nickel depends on the relative
positions of these elements in the Periodic Table.
A number of multi-component nickel solid solutions were
synthesized for that work (the crystal-lattice type7
atomic diameter and solubility in nickel are tabulated).
In the present work the equilibria and some physico--
chemical properties of solid solutions in the following
systems were studied: 09 Ni-Al; 1, Ni-Cr-Al;
II) Ni-Cr-Ti-Ali III, Ni-Cr-Ti-W.-Al; IV, Ni-Cr-Ti-W-
Mo-Al; V, Ni-Cr-Ti-W-Mo-Nb-Al; VI, Ni-Cr-Ti-W-Xo-Nb-
Card co-Al. In each system one section with 0-12% Al and a
1/3 constant quantity of otheir elements, except nickel, was
studied: 10 wt.% Crj'2 of Tiq 6 of W, 3 of Mo, 2- of Nb)

69660
1;/180/60/000/02/016/028
Hill/E152
Properties of Multi-Component Nickel Solid Solutions
5 of Co. The fusion diag,rams for these systems were-
studiedq the Al solubility limit being determined by
microstracture, X-ray, hardness and electrical
resistivity methods. The :results for each system are
plotted against wt.% aluminium In Fig 1. Fig 2 shows
miarostructures of one- and two-phase systems after
hardening from 1200 OC. The lattice parameters for the
solid solutions at 1200 OC as functions of aluminium.
r,ontent are shown in Fig 3. The resistivity of alloys
after annealing and their hardness after hardening from
1200 OC are shown as functions of aluminium content in
Figs 4 and 5. respectively. In this work the limiting
concentrations of the elements were determined and the
nature of the excess phase,s established. The degree of
strain in the solid-solution crystal lattice increases
with increasing difference between atomic diameters of
the introduced element and of nickel. In order of
Card decreasing lattice'-disturbing effect the elements are
2/3 Nb7 Wt Tit Mot Cr and Co. The hardness of nickel solid,/
solutions could be increased considerably by L

69660
3/180/60/000/02/016/028
111/9152
Properties of Multi-Component Nickil Solid Solutions
multi-component alloying with those elements which
increase the-state of strain of its lattice.
There are 5 figurest 1 table and 2 Soviet references.
SUBMITTED: June 249 1959
Card 3/3

OOOQ1. 7 8 -1.3 1,
S 0 v/ i r2 o - 6 o - 3
AUTHORS: Kornilov, I. I., Ivanova, V. S.
TITLE: At the International Symposium on Problem2 of Developing
Heat-Resistant Material,,,
PERIODICAL: Metallovedeniye- I tenrilcheskaya obrabotka metallov,
1960, Nr 3, PP 58-60 (USSR)
ABSTRACT: An International Symposium on the above problemo was
initiated by the Learned Council of the Czechoslovakian
Scientific and Technical Society (Nauchiiyy oovet
Chelchoslovat-skogo nauchno-telchnicheskogo obshchestva"
It took place at Marianske Lazne (Czechoslovaic-ia) from
September 11 to 13, 1959. Seventy scholars from Czech-
oslovalcia, the USSR, the GE-rman Democratic Republic, France,
Switzerland, Australia, Belglum, Sweden, China,Poland,
Austria, and England participated in the'symposium. The
Soviet Union was re-resented by the authors as well as by
M. V. Pridant3ev, Professor and Doctor of' TechnicalSeienew-)
and A. I. Chizhik Mndldate of Technical Sciences). The
Card 1/2 agenda Included such subjects as (1) creep theory

At the.. InLE5rnational Symposium on Problems
of' Developing Heat-,Resistant Materials. SOV/129-6o-3 -13/16
and 2tre2rj-rupture; (2) low-alloy and modified
stalnle~ss heat-1,ei3istant (3) uu~,3teliltlc
steels; (4) heat-re2istarit and speclaJ alloys;
(5) modern methods of devc.,Ioplng heat-re3istant alloyo;
and (6) control and evalii;.,Ltion methodo to determine the
applicability of heat taiit matevlal,,. The SovIet
scholars submitted the following reports: I. I.
Kornilov, "Basic Types of' Composition vs Heat-Resl3tance
Diagrams"; I. A. Oding, V. S. Ivanova, and Yu. P.
Liberov, "Effect of Parting.Plane Surfaces on Protracted
Failure.of Metals"; M. V. Pridantsev, "Problems of
Steel and Alloy Heat-Resistan-Ce. " The papers and
dl2cu3slons of' the symposium are published in a
supplement to the journal Hutnicky Listy, Nr 12 (19r-O".
Card 2/2.

S/18060/000/03/012/030
AUTHORS: Kornilov I.I., Mikheyev,oi'.~WM Chornova, T.S. (Moscow)
TITLE: Study of the Partial Phase Diagram of Titanium-alumini=-
T1 chromiuml~-ron-silicon d - - 0
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurglya i topliv.o, 1960, Nr 3, pp 70 - 72
+ I plate (USSR)
ABSTRACT: Kornilov has previously war 'ked on the reactions of titanium
with various elements (Refs 1-3) and the phase diagrams of
some binary and ternary titanium base alloys (Refs 4,5)-
In the present work experimental data from his) nd his
co-workers' study of the p!irtial phase diagram4or the
five-compcmnt Ti-Al-Cr--Fe--fii system are presented. The
diagram is represented by the t-etrahedron method (Ref 6)
in which the origin is takian as 'the composition of the
solid solution (here the alloy corresponding to the binary
Ti-Si solid solution with 0.5 wt.% Si is taken), the three
remaining components being assigned to the three axes
(Figure 1). As shown in Table 1, aluminium has a high
solubility in both alpha-and beta-titanium, that of the
others being small in alpha-titanium. Grade TG-00 titanium
Cardl/2
L-I~c

86071
n I S/180/60/000/005/012/033
E193/E183
AUTHOR. Kornilov, I.I. smoscow)
TITLE- Some Problems of the Theory of High Temperature
Stre4g~~4, and the Development of New High-Strpinpth
'Titanium-Base Alloys.,I(Basic Types oi une
Composition/High-Temperature Strength Diagrams)
PERIODICAL: Izvestiya Akademii nauk SSSR,Otdeleniye tekhni-ciieskikh
nauk, Metallurgiya i toplivo, 1960, No.5, pp.128-132
TEXT: The author of the present; paper correlates the high-
temperature strength of alloys with their constitution diagrams
and describes three main types of the high-temperature strength/
-omposition diagrams. Type I corresponds to the -systems which
form continuous series of solid solutions with, or without, solid
state transformations, In the absenae of solid state transfor-
mations as, for instance, in the Au-,Ag, Cu-Ni, Ni-Pd, Ti-Mo,
Ti-Nb, Mo-W, V-W systems, the high-temperature strength increases
gradually with increasing concentration of either component,
passes through a flat maximum and then decreases again. This
holds true even at temperatures equal 0.6-0.8 T, where T is the
Card 1/4

86071
S/180/60/000/005/012/033
E19VE183
Some Problems of the Theory of High-Teraperature Strength and the
Development of New High-Strength Titanium-Base Alloys, (Basic
Types of the Composition/High-Temperature Strength Diagrams)
melting point of the low melting point component, i.e. at
temperatures considerably higher than the rearystallization
temperature of these alloys. The position of the maximum
depends on the high-temperature properties of the components and
is usually shifted towards the higher concentrations of the
component, which has relatively higher strength at elevated
temperatures. In the case of systems represetting continuous
series of solid solutions, in which salid state transformations
take place (e.g. Fe-~Ni. Mg-Cd, Au-Cu, Fe-Cr, Fe-V, Fe-Pt,
Fe-Pa), the high-temperaturie strength of the alloys at
temperatures above the maximum transformation temperatures varies
with composition in the manner deserroed above, At temperatures
at which the two components no longer form a continuous series of
solid solutions, the high-temperature strength increases
gradually with increasing concentration of either component and
then rises sharply to a point maximum., situated usually at a
Card 2/4

36071
S/180/60/WO/005/012/033
E.193/E183
Some Problems of the Theory of High-Temperature Strength and the
- of New High-Strength Titanium-Base Alloys. (Basic
Development
Types of the Composition/High-Temperature Strength Diagrams)
composition corresponding to an intermediate phase, intermetallic
compound, or an ordered phase, Type II of the high-temperature*
strength/composition diagram corresponds to the eutectiferous.
systems with a wide range of solid solubility at each end of the
constitution diagram and with the solubility in these ranges
increasing with rising temperature(a.g, Al-Mg, Ni-Cr, Ni-W
systems), In this case, the high-temperature strength/composition
curve has two sharp maxima corresponding to solid solutions with
the maximum solute content, irresDecti've whether the solute is an
elementl intermediate phase, intermetallic compound, or a solid
solution. In the composition range between the two maxima, the
high-temperature strength of these alloys changes linearly with
increasing concentration of the II-nd phase, Generally speaking,
the high-temperature strength of the 2-phase alloys is higher
than that of either phase, but lower than that of the solid
Card 3/4
86o7i
8/180/60/000/005/012/033
E193/El83
Some Problems of the Theory of High-Temperature Strength and the
Development of New High-Strength Titaniim-Base Alloys. (Basic-,
Types of the Composition/High-Temperature Strength Diagrams)
solutions with the maximum solute conteats, Finally, type III
of the high-temperature strength/composLtion diagram oorresponds
to the eutectiferous systems with no', or very narrow, solid
solubility ranges (eg. Ou-Cr' CU-Zr , Ni-Zr, etc,,,, systems),
In this case the high-temperature -strength of the alloys
gradually increases with increasing concentration of the component
which is stronger at elevated temperatures,
There are 3 figures and 15 Soviet references,
SUBMITTED: February 23, 1960
Card 4/4

86072
141b S/1.80/60/000/005/013/033
I Z 2_0 () EO'113/E535
AUTHORS.- -Korn-ilov, 1. 1. and Nartova, T. T. (Moscow)
V1
TITLE: Refractoriness of Alloys of the System Titanium-Tin
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1960, No.5, PP-133-136
TEXT., In earlier work (Refs.1-4) the authors established the
relations governing changes in the properties of titanium alloys as
a function of the chemical composition and the character of the
diagram of state. In this paper the ritsults are described of
investigations of the high temperature strength of binary Ti-Sn
titanium alloys.From results obtained -.n investigating the diagram
of state it was established that a.coni3iderable Sange of solid
solution of tin in a-Ti (up to 21 wt.% Sn at 700 C) exists. The
two-phase cc + y range extends at 700 C to about 42% Sn; for a
content of 45.24% Sn in the Ti-Sn system, Ti Sn compounds form. In
addition to investigating the structure and & properties of alloys
of this system., the authors studied the high temperature strength
of binary Ti-Sn alloys from the range of a solid solutions and the
two-phase a + y range with a tin concentration between 0 and 30 wt.%.
The high temperature strength of alloys with over 30 wt.% Sn was
Card 1/4

86o-, a?
S)'180/60/000/005/013/033
E073/E535
Refractoriness ofAlloys of -the System Titanium-Tin
not investigated with the exception of the alloy corresponding to
the y,-phase, the Ti Sn base solid solution. The alloys were
smelted in an are farnace in an argon atmosphere from a charge
consisting of titanium sponge of 99.8% purity and a specially
smelted Sn-Ti alloy containing 69.5% Sri,, Alloys containing up to
25% Sn were forged at 900 C and annealed in vacuum with stop-wise
cooling in accordgnee with the following 0regime: 50 hours at 110000,
100 hours at 1000 C and 200 hours at 8130 CI) followed by slow cooling
in the furnace down to room temperatur.a. The microstructure of the
specimens, which was investigated after the high temperature tests,
had either a single-phase structure of a and y solid solutions or
a two-phase a + y structure. Some characteristic microstructure
photographs of the studied alloys are reproduced, The composition
of the etching agent was. 25% HF1 25% HNO and 50% glycerine.
Investigation of the high temperature strhgth of binary alloys was
carried out by the centrifugal method in four st5ges; in each of
these stages the same bending stress of 15 kg/mm. was applied.
During the first stage., the specimens were stressed for 100 hours
Card 2/4

86072
S/'180/60/000/005/013/033
E0?3/E535
Refractoriness of Alloys of the System Titanium-Tin
at 500 OC, then the temperature was raised to 5500C and the tests
were continued for another 100 hoFs (second stage), Following that,
the temperature was raised to 600 C and the tests continued for
1000hours (third stage) and, finally, the temperature was raised to
650 C and the tests continued for another 100 hours (fourth stage).
This regime was chose in view of the very low high temperature
strength of titanium 4rarefied solid solutions oT titanium and its
two-phase alloys on the one hand, and the high strength at elevated
temperatures of alloys in ~ the range of concentrat-ed, saturated and
slightly over-saturated solid solutions on the other hand, On the
basis of the obtained data, the creep curves of alloys of various
compositions are plotted for all the four stages of investigation,
It was found that the high temperature strength of Ti-Sn alloys
increased gradually with increasing concentration of the tin in the
a solid solution and the maximum high temperature strength is obtained
.for alloys whose composition approaches the limit solubility (18 to
22% Sn). Alloys with a clearly pronounced two-phase structure have
a low high temperature strength, due to the coarse inclusions of the
second phase. The Ti Sa base alloy had the highest high temperature
strength at all the a;plied test temperatures. The results obtained
Card 3/4
86072
1.)/180/60/ooo/oO5/013/033
1,1073/E535
Refractoriness of Alloys of the System Titanium-Tin
on investigating the high temperature strength of binary Ti-Sn
alloys are in good agreement with earlier established relations V~
governing its changes in the metallic systems (Refs.1-4 and 6-11y,
There are 3 figures and 11 Soviet references.
SUBMITTED: February 23, 1960
Card 4/4

86073
si/180/60/000/005/01.4/033
E073/r',535
AUTHORS: Lorailov~ I. I., Ozhimkova., 0. V. and Pryakhina,
(Moscow)
TITLE-. Relations Between thej Composition, the Temperature and
the H~Rh Temperature'%Strer.gth of Alloys of the System
-YIN-*Lcke1-Q_hZ2_m_ium-Tun9st n-glitanium-Alumini m0
PERIODICAL: Izvestiya AkadAii nauAsSR, OtAleniye tekhnicheskikh
nauk, Metallurgiya i toplivo, 1960, NO-5~ PP-137-141
TEXT: The aim of the here described work was to study the
dependence of the diagram "composition-high temperature strength" on
the test temperature and the composition of alloys of a 5-component
system Ni-Cr-W-Ti-Al for a variable Al content. For investigating
the properties of some alloys of the Ni-Cr-W-Ti-Al system, one V~
polythermic cut was taken of the alloys with a.constant content of
Cr9 W1 Ti and a variable content of Al (from 0 to 16%). Increase
in the Al content proceeded as a result of a drop in the Ni content.
Basically, the alloys of this section correspond to quaternary
uniform solid solutions. It can be seen from the fusion diagram
that addition to Al bSings about a redu8tion of the liquidus
temperature from 1430 C (0% Al) to 1275 0 (16% Al). For contents
Card 1/3

W73
E/180/60/000/005/014/033
E'073/E535
Relations Between the Composition, the Temperature and the High
Temperature Strength of Alloys of the System Nickel-Chromium-
Tungsten-Tita.nium-Aluminium
of 6.5% Al and more the cooling curves show a second step, which
corresponds to the crystallization of the second phase that separates
out in the form of a eutectic. For dotermining the solubility of
Al in the nickel solid solution, the following heat treatment was
applied; soaking for 100 hours at 1200 () C, queaching in water wi th
subsequent soaking at 1100, 1000, 950 jand 800 C for 1000 hours,
followed by cooling in water. The com:oositions of the alloys were
in the range of quinquary nickel-base solid solutions and rejection
of the excess y'-phase (on the basis of the Ni Al compound with
a face-centred cubic lattice). Presence in al oys of the y-phase
was established by inter-metallide and X-ray structural analysis.
It was established by micgostructural analysis that the 0 solubility
of Al equalS 5.5% at 1200 C, 4.20/6 at 1100 C, 3% at .1000 C and
2.2% at 800 C, The influence of temperature on the strength of the
alloys was investigated on alloys with Al contents between 0.5 and
7.9yo that correspond to uniform solid solutions as well as to two-
chase alloys. The test specimens were produced by precision casting
ard 2/3

86073
S/180/60/000/005/014/033
E073/E535
Relations Between the Composition, the Temperature and the High
Temperature Strength of Alloys of the System Nickel-Chromium-
Tungsten-Titanium-Aluminium
and subsequent soaking at 1150 0C for 7 hours, followed by cooling
in air. Study of the high temperature strength was effected by
applying the centrifugalbending method at the following initial
stresses a'k t?0C J7001 Boo) 950, 1000, 1100, 1200
6/mm 501) 30-40t 15, 10~ 3, 1.2
It was established that at 12000C the maximum, high temperature
strength is obtained for alloys which correspond to strongly 0
rarefied solid solutions; in the temperature range 1100 to 1050 0
the highest strength was obtained for alloys that are distributed
along the line of liWit solubility and regions adjacent to iti at
temperatures of 1000 C and lower, the highest strength was obtained
for alloys from the range of saturated solid solutions that contain
rejected finely dispersed excess phases. There are 3 figures and
4 Soviet references,
SUBMITTED: April 1, 1960
Card 3/3

KORNUOV. I.1.; POtTAKOVA, B.S.
Investigating the beat resistance of platinum alloys with rhodius.
iridium, ruthenium, chromium and aluninum by the flexure metbod.
Trudy Inst.ust. no.5:139-144 060. (KIRA 13:6)
(Beat-resistant alloys)
(Platinum alloys--Testing)
(Flexure)

KORIUIOV, Iol.; PRYAKHINA, L.I.; 09HIMWFA, O.V.
Atfect of the time factor on the characteristics of the constitution -
heat-resistance diagram of five-component alloys in the system Ni -
Or - W - Ti - Al. Isol. po sharopr., oplav.6*.278-283 160,
(MIRA 13:9)
(Alloys--Thermal ivoperties) (Phase rule and equilibrium)

/JD TIS 69056
AUTHORS: lornilovo I. I., Nartova, T. T. S/07SJ60/005/03/021/048
'A B004/BO15
TITLE: The )?he *_Diagra of the System Titanium -4in
PERIODICAL% Zhirnal neorganicheskoy khimiij 1960, Vol 5, Nr 3, pp 622-629 (USSR)
ABSTRACT: The study of.th* ternary systemli - Al - Sn induced the autho re
to investigate the phase diagram of the system Ti - Sn including
the compound Ti 3Sn (0 - 25 atom~lof Sn). Figure I shows the equi-
libtium diagrams of this system in the region of a " P transforua-
tion as taken from publications (Refs 6-10). The auThora point out
the contradictions of these data, The raw materials were titaniun
metal of the type TO-O (99-7% of TO and tin (99## of Sn). The ale-
loys were zolten In the are In argon atmosphere for the purpose
of structural analysis, thernal analysis, and hardness tests Alloys
produced by way of powder metallurgy were used for the purpose of
measuring the electrical resistance and testing the thermal etabili-
ty. The authors describe in detail the homogenization. of these
alloys. Figure 2 shows the thermograms recorded by a Xurnakov pyro-
meter. The temperature of the.a transfor tion of solid solu-
tions (Table,l) passes through ~" minimum (86? ) at 5 atom$ of fto
after which it rises (20 atom% Of Sn) to 890 , at which temperature
the peritectic reaction cc --+ P + y occurs. Table 2 shows the
Card 1/2 microstruotures of differently tteated alloys with varying tin con-
Card 2/2

69o25
/P j/00

AUTLORS: is
Bi Tain-khual ~prnilovt.l 8/078160/005/04/022/040
. : ~ Mo4jbo16
TITLE: Investigation of the Phase Di~irJ of
the Syste,~ We - Lvi
PERIODICAL: Zhurnal neorganichookoy khimiip 1960t Vol 5t Kr 49 pp 902 - 907
(USSR)
ABSTRACT: The authors investigated the quavibinary section TiFe - V of the
ternary system Ti - FeVL V by meems of thermal analysis, micro-
structural analysis, radiograms, and hardness test. Tile was
prepared from TG-O titanium and Armco iron. The 22 investigated
alloys with a content of 3 - 90 irt% of V were obtained by melting
from TiFe and vanadium powder by the method of powder metallurgy.
Table I given the melting points of the individual allo a from
which the phase diagram TiFe - V was constructed (Fig 1~. The
diagram only gives the solidue line. The liquidue line was not
investigated. The microstructure;t of the alloys treated in a dif-
ferent way revealed that the distribution of the phases in inde-
pendent of the thermal treatment (Table 2# Fig 2). X-ray analysis
was carried out by L. N. Guseva (Fig 3, Table 3) and confirmed
the data of the microstructural analysis. The hardness test was
made by means of a Vickers devico, diamond pyramid, and a load of
Card 1/2 10 kg (Fig 4). In the system investigated the authors detected a

Inveratigation of the Phase Diagram of the Systom
TiFe V
SUBMITTED:
69025
8/078/60/005/04/022/040
B004/BO16
ternary compound (TiFe)V which lis formed by peritectic reaction
and occupies a small regio4 of solid lutions. Th a GOU-
pound has a hexagonal lattice with & !"M-86410 a - . - 10
c/a - 1.63, and a hardness of about 800 Etv. The system TiFe V
has three regions of homogeneous solid solutions (69 y9 and
on the basis of TiFeq (TiFe)Vj and V and two diphase regions
(6 + y and y + P). The solubility of compound (TiFe)V in V in-
creases with increasing temperaturet whereas the solubility of
TiFe in the solid gamma solution changes but little with in-
creasing temperature. The present paper provides the foundations
for the investigation of the influence exercised by compound
(TiFe)V upon the propertiea of vanadium# and for the investiga-
tion of the phase diagram of the ternary system Ti - TiFe - Ve
There are 4 figures, 3 tableal aftd 5 references# 2 of which are
Soviet*
January 239 1959
Card 2/2

4~
B004/BO14
S 7 t1
AUTHOU: Kornilov, I. I., Matveyevaq No M.
TITLE- Reaction Ileat of the TransItion of the c-Phase Into the
solid a-SAution in the Systenl):Irron Ahromium
PERIODICAL: Zhurnal neorganicheskoy khimii, 1960v Vol. 5.,, No. 61
pp. 1367 - 1388
TEXT: By way of introduction, the authors describe the thermographic
method which they used for their experiments. This method was suggestAft
by L. G. Berg and V. Ya. Anosov (Refs. 1 and 2), and was improved by
G. G.Tsurinov (Ref- 4). A substance which does not react with the sub.-
stance to be tested,"and whose thermal el 'Tects are exactly kn,')V7n ser'Ves
as standard substance. Its thermal differential curve is recorded by a Y
Xurnakor pyrometer along with the differential curve of the substance to
be tested. The values of these thermal effects are obtained by graphice-.1
integration of the deviations from zero and on the strength of the known
values of the standard substanoe, The prosent paper describes the tranu-,*~'
tion of the 6-phase (composition of the alloy similar to that of FeCr)
S/078/60/005/o6/28/030
Card 1/2

Reaction Heat of the Transition of the d4hase S/078/60/005/06/28/030
Into the Solid a-Solution in the System B004/BO14--
Iron - Chromium
into the solid a-solution. The alloys were made from electrolytic
^hromium and Armco iron in an are furnace filled with argon. Then, they
were homogenized and annealed for 500 - 700 hours at 7000C in order to
obtain the a-phase. Iron with an a -3~p transformation equal to .
0.27 kcal/gram-atom and a P -~V transformation equal to 0.25 kcal/Cram-
atomjwas used as standard. The endothermic effects of the cf->a transforma-
'tionPof the Pe-Cr alloy are between these two effects of the standard
iron (Fig. 1). Analyses of the alloys under considerationg as well as
their temperatures and heats of transformation are given in a table.
The heats of transformation varied between 1.06+0.05 and
0-73�0-05 koal/gram-atomp depending on the com;7osition of the 6-phase.
There are I figure, I table, and 7 references: 6 Soviet and I British.
SUBMITTED: January 6, 1960
Card 2/2

83125
8/078/60/00 5/009/00 6/017
B015/BO64
AUTHORS: Kornilov, 1. 1.,. vlasoy, Y. S.
TITLE; Investigation of the Physicoohemical Properties of the
Alloys of the Ternary System Tltaniun - Vanadium - Niobium
-i ~-- A- ii
PERIODICAL, Zhurnal neorganicheskoy kh1mki? 1960v Vol. 5~ No. 9.
pp. 2017-2024
TEXT., The electrical. resistivity, its the.rmal coefficient, thermal ex-
pansion, and the hardness of the systems Ti-Nb and Ti-V-Nb were investi-
gated. The thermal preliminary treatment of the samples was done in two
ways. The electrical resistivity was determined at 20 0 and 1000 C with a
nnT,B(PPTV) potentiometer. The hardness was investigated an samples that
'were subjected to microstruotural analysiso The samples were annealed
at different temperatures in accordance with the titanium content, On the
basis of the phase diagrams obtained, a similar depepdence of the elec-
trical resistivity and temperature coefficient on the composition were
found to exist in the titanium corner of the phase diagram of the three-
component system. as well as the two-component system. Thq diagrams of
Card )/2
:
83125
Investigation of the Physicochemical Properties S/078/60/0()5/009/008./017
of the Alloys of the Ternary System Titanium - B015/BO6'4
Vanadium - Niobium
the Qiermal expansion of the ternary system in the range of q ^omDoi
V , Nb showed that in the two-phase range there aro_,
an irreg0nr r-hange f)f 0XpanvionRi'e., where the most intenz-ive P .hqs-
txans-'ormation takes place, The temPeratr-e of tnese sclitjon.,3 decreaso!3
vith the incrPase of the ranadium- Rrd niobium concent, whicr ~,,rr;~sprn
~ne rhase diagrams Line. V~
q of the same hardnpss, 1.e., iqoqcler;,~
Of th-1 ;eotherma! cross seotion for 6000
C were drawn on thp diarram ni' tri-
sys'.I~m T-V~Nb ancording to the values of hardness measurpmen,
C~ange of" hardress is also dependent on th-? phase 9-rructure. The oDtimum
OOmPOsitions of the alloys on the basis of' (Y- and 0-phases with ce'rta:!"
properties can be determined on the basis ef the phssc diagram's, There
are .9 figares and 10 references: 7 Soviet and 2 US.
SUBMITTED: June19, 1959
Card 212

S, to
AUTHORS:*,,
TITLE:
69508
Kornilovol.I09 Wartova,, T. T. S/020/60/131/04/033/073
B010017
Equilibrium DiaRramlof the Ternary System Tj 41_- Sn
PERIODICAL: Doklady Akademii nauk SSSRv 1960, Vol 131, Nr 4, PP 837-839 (USSR)
TEXT: Since. no data are available in publications on the diagram mentioned
in the title, the authors studied the equilibrium of the alloys of the mentioned
system in the range limited by the partial ternary system Ti - Ti 3Sn - TiAl. The
binary systems Ti - Al and Ti - Sn which form the latter ternary system show
that in these two gysteme limited solid solutiorce are formed on the basis of
a-titanium at 1240 in thesystem Ti - Al (due to periteotoid reaction between
the 0-phase of titanium and the y-phase on the tasis of the TiAl compound); these
solutions are formed between the 0P-phase of titanium and the 6-phase (on the
basis of compound Ti3 Sn), at 890 in the system Ti - Sn. For their investigation
the authors employed the microstructural X-ray method and the hardness test
of alloys. Several alloys were forged to accelerate the establishment of equi-
librium. Theg were subjected to gradual thtrmal treatment in the vacuum: h8mogeniza-
tion at 1220 for 100 hq annealing at 1100 for 50 h$ 10000 for 200 hq 600 for
300 h, 600 for 500 h, and then left to cool in the furnace. Ti 3Sn - TiAl alloys
were annealed for a longer period, and cooled slowly. The phase diagram (Fig 1)
Card 1/3

69508
Equilibrium Diagram of the Ternary System Ti - Al - Sn 8/020/60/131/04/033/073
BOII/BO17
Vag0drawn on the basis of part of the Ti Al - Sn system investigated at
600 . The follovinf.5hases were observed: 1) Solid solution of aluminum and
tin in a-titaniusi ; 2) solid solution on the basis of the chemical compound
TiAl (1); 3) continuous solid solutions of thecompounds Ti 3Al - T13Sn which are
.in agreement-as to their structure with the s- and 6-phaves; 4) so~-~4 solution
on the basis of the chemical.-compound Ti3U (6).' As is hown by fi6m - 1, the
main part of the diagram oonsistai.of the -one-phase ran:e of the 8011,.~-ternary
a(6)-solution on titanium basisp and on- the basis of the quasi-binary cross section
Ti Al - mi3Sn. Between the latter compounds continuous solid solutions are formed.
Alloys with a two-phase -structure a+6 (Fig 2b) were, in view of a possible forma-
tion of continuous solid solutions between *-titanium and Ti Sn, additionally
3
annealed at 8000 (for 1,000 h). Hence, their microstructure was slightly changed.
Thus, the given conditions at which the state of equilibrium is attained are
characterized by the presence of a two-phase range a+6 which adjoina the side
Ti - Sn of the diagram. As may also be seen fromthe diagram, the range of the
solid I-oolution is considerably extended (~b to 18% of Sn). In the part of the
diagram investigated, no 3-phase range was observed. There are 2 figures and
8 references.
.Card 2/3

81703
8/02oJ60/132/05/31/669
73-0 0 BOI1/BI26
AUTHORS: K!Kornilov" 1. 1.9 Pry in&, L. I., Ozhimkova, 0. V.
TITLE: The Influence of the Time PLotor on the Character of the
Composition - Beat Resistanoe Diagramil)f Alloys of the
Ni - Cr - W - Ti - Al Five ("lomponent System
1-1 -Vi 1A
PERIODICAL: Doklady Akademii nauk SSSR9 1960, Vol. 132, No. 5,
pp. 1086 - 1089
TEXT: The authors wanted to examine the ipimultaneous influence of the
composition and a long conversion time on the heat resistance of alloys.
With this object in view, they studied tho creeping of alloys of one of
the crose.-sections of the above systeav with Ni replaced by Al, within
0 to 7-9%9*and with a constant Crq W9 and Ti contento The phase diagram
of the cross-section analyzed is given in Fig.-I. In order to examine
creeping, the sasples were heated to 1150()Cp--maintained at this tempera-
ture for seven hourev and then coolld in air. After such homogeneization,
the compounds with up to 5-1% Al.showed a structure of solid five-com-
Ponent solutions with a small quantity of excess I Ophaseq which was
Card 1/4

81703
The Influence of the Time Factor on the S/020/60/132/05/31/069
Character of the Composition - Beat B0111B126
Resistance Diagram of Alloys of the Ni Or - W - Ti - Al Five Component
system
separated due to the cooling in air. Above this Al oontentp an eutectio
appears, consisting of solid y-solution amd the-11-phase. The alloys
were analyzed for creeping by the centrifugal method at 9000 with an
initial tension of.6 kg/fim2. Proa the curves in Fig. 2 it can be seen
that the alloys with a high Al content (6.5 and 7.9%). whose composition
domes in the range of common crystallization of the solid y-solution
and the eutectic, have proved themselves to be not resistant to heat.
From the curves in Figs. 2 and 3 it follows that an alloy with a maximum
supersaturation (with 5.1% Al) for a.short deformation-time (300-400
hours ),, i. the most heat-r*sistant. if the time is increased to 700-800
hourap th:n alloys with a lesper degree of supereaturation are the most
heat-resistant (3-49 2.89 and 1.8% Al)s, which lie on the border of the
maximum aluminum solubility. On further 'tests for creeping of up.to
10,000 hours durationg the whole charaot,ir-of the curves for single
alloys does not change, except in alloys with 2.8 and 3.4% Al. This
shift of the heat resistance maximum in -the phase diagram is due to the
Card 2/4 , 4/

The Influence of the Time Pactor on the
.Character of.tho Composition - Heat
Resistance Diagram of.Alloys of the Ii.
System
81703
3/02oj6o/132/05/31/069
Boil/B126
Cr - W - Ti - Al Five Component
influence of the time factor on the physioo-ohemioal conversion proo-
eases and on the structure changes of the alloys during the tests. The
alloys with maximum supersaturation haveg on a short testq the highest
solidity, since the Inner tensions in the lattice of the solid solution
are great. This solidifying effect decreases in the-range of less super-
saturated solutions and in the range of the formation-of euteotic mix-
tures on crystallization. on longer tests the solidifying also de-
creases due to the varied effect of the time factoro The solidification
deareasee.even more, the higher the degree of supersaturation and the
longer the duration of the test. In the latter case, diffusion processes
also take effecto The formation of an excess phase, and its subsequent
oqagulation lower the heat resistance. Thus the authors have proved
that the beat resistance maxima in the loothezaia diagrams composition
versus heatresistance are dependent on both temperature and time.
Kurnakov coinpounds are mentioned. There are 3 figures and 9 referenoes:
5 Soviet, I British, and 3.1merican.
Card 3/4

AUTHOR:
TITM
PERIODICALs
8705
B/020/60/135/006/021/037
B016/B060
Metallochemical Properties of Niobium,
Doklady Akadem-4i. nauk SSSR, '1960p Vol. 135, No. 6,
pp. 1399-1401
TEXTa The author describes the metallochemical properties of niobium and
classifies the elements of the periodic table into groups according to
their chemical interactions with niobium. According to data found in the
literature, niobium as a metal of the transition group has an unfilled
outer d-electron shellq and its at OM4C radius 1-45 A is very close to
that of nearby metals. As for electronegat-141-vity, Wb occuples an Inter-
mediate position In the metal series (Reef- 5). About 35 metals are electro-
positiv;~ with respect to -N~, while 37 behave electronegatively with it.
Its lattice is body-centered. Fig. 1 shows a periodic table by D. 1.
Mendeleyev as modified by the authoi, with Nb being placed on top out-
side the table. All other elements are divided into four "families":
1. 8 metals forming continuous solid solutions when crystallizing with Rb,
Card 1/4

87405
Metallochemical Properties of Niobium S/020160/135/006/021/037
B016/B060
and whose metallochemical properties diverge little from those of.Nb. They
are Ti, Zr, V, Ta, Pa, Mo, W, and U. 11. Th-l~i famLly encompaSSe5 a large
grcup of elements forming limited 8014d solutions with Rb. Outside the
range of solubility, compounds with a metallic character of the bond are
formed with Nb. They are a total of 56 when all lanthanides are included,
and 68 when taking in also all. the 10 actinides. From among the 68
elements of family II the interaction with Nb has been investigated for
27 elements only. The peak solubility of these elements in nioblum drops
wi.th in-reasing di-vergence of their metallochemical properties from
nioblum. The compounds of niobium with metalloids (borldes, carbiies
silicides ol" niobium) have a metall1i type of bond. This holds also for
the vezy Iimlted solid solutions and compounds -if nioblum w-Itb N, P, As,
Sb, and 0. The deg-ree of metallic pr3p,~r'fes of these Nb compounds r1ses
with increasing d1-11"ference between th-~'r- m0-,Alochemical properties and
those of niobium. III. This famfly c,~mpriseo 9 typical which
are the most strongly elec~r-').neigativo. They form no solid solutions with
ITb, but only compounds with covalent ionic bonds. Oxygen occupies an
intermediate position. IV. This family comprises 16 elements of the first
and second group of the periodic system (bydrogen and beryllium excepted)
Card ?/4

87405
Metj~Fjlochem:ical Properties of Niobium S/02oj6o/135/006/021/037
B01 6/B060
as well as the inert gases. These elemerits exhibit no interaction with 1,Tb
and form no compounds with it. It is firtally noted that the concenturations
of the components in niobium systems cart be calculated on the basis of the
classification of the individual elements under I and 11. Also alloys with
given structure and properties can be produced. There are 1 figure and
6 referencest 5 Soviet-
ASSOCIATION: Institut metallurgil im. A. A. Baykova Akademii nauk SSSR
(Institute of Metallurgy dmeni A. A. Baykov of the Academy
of Sciences, USSR) -4-
PRESENTEDt June 279 1960, by 1. 1. Charnyayevf Academician
SUBMITTED: June 14, 1960
Card 3/4

87405
S/020160/135/006/021/037
Bo16/Bo6o
.
CN 1,
;

-5 6
M 15- fo 17 0

r n

iBei
B c
N 01
e
L___j _j
'Al Si 1) S I I

CD~ i Sc; Ti V
v I C, AM Fe Co Ni Cu Zn Gn Ge As; SL r

r Y:: zr Tc Ru Rh I'd Ag Cd In Sii Sb; e

I T- W ;Re Jr Pt Au I p0 At:

Ra IAc Th
"
Y
A I A
[]I Oil Emill EIV
Card 4/4

KORNIWV, I.I.; BUDBZMv P.B.; SORMIDYA, N.Vp tekhn. red.
[Phase diagramA or two-4td-Urbe-dcoponent, systems of titanium]
Diagrammy sootdimiia ftolv7Mi i trc-itykh slatem titans. Mookvir
Vaes. in-A nauabnoi i tekhn. infornataii, 1961. 172 Pe
(MIRA 14t6)
(Titanium alloys) (systems (Chemistry))

0A
Korniloyt, Ivan Ivanovich
PUN I BWKmaW=ATIO1q
SOV/594,6
Fiziko-khim-tcheskiye oanovy zharoprochnosti splavov (Physical and Chemical Bases
for the Heat Resistance of Alloys) Mosdow,,'Izd-vo AN SSSR., 1961. 515 P.
Errata slip inserted. 32M copies prizvted.
Sponsoring Agency: Akademiya nauk SSSR. Institut metallurgii imeni A. A. Baykova.
Resp. Ed.: I. A. Oding,, Corresponding Member., Academy of Sciences USSR; Ed. of
Publishing House: S. G. Fedotov; Tech. =16-:., P. S. Kashina, and Yu. V., Rylina.
PURPOSE: This book is intended for physicists,. chemists,, mtallurkists.. metallo-
graphersp and technical personnel engaged lit the study,, production, and appli-
cation of heat-resistant materials, It may also be useful.to aspirants at
scientific research institutes and schools of higher educatien and to stuilents.
Physical and Chemical Bases (Cont.) SOV/5946
strength and heat resistance of yam metals and alloys of single-component and
multicomponent systems and to basic problezis of the physicochemical theory of
heat resistance. The book is based primarily an experimental material on the
problem of heat resistance collected over a period of 10 to 15 years by the
author and a group of workers of the Laboratory of the Chemistry of-Vietal
Alloysp Institute of Metallurgy imeni A. A. Baykov. For purposes of analysis
and generalization, m1merous Soviet works and non-Soviet vorks have been utilized.
TABLE OF COITnWS:
Introduction
Ch. I. Methods of Investigating Beat Resistance
1. Brief characteristics.of beat resiotancc,
2. Standard testing methods
3* Rapid testing methods
4. Centrifugal testing method
Conclusions
Bibliography
Ch. II. Properties of Metals of the Periodic System of Elements
1. Metals and metalloids of the periodic system.
C
89vt-A
5
5
6
a
15
38
59
41
41

Equilibrium of the ternary system
699o6
S/062/61/000/002/001/012
B115/B207
solubility of Ni 3Ti - Ni 3Ta - Ni3Nb indicates, for the compound Ni 3Tit
the possible existence of a second high-temperature modification of the
P - Cu3Ti type rhombic syngony, as it is the case with the compounds
Ni3Nb and Ni3Ta. The authors stress that no published data exist on t/,
the equilibrium in the mentioned ternary system, apart from a brief
mention of the possibility of formation of continuous, solid solutions.
Fig. 2 shows the composition of the alloys studied. A table provides
data on the thermal analysis and the stability of alloys of the
ternary system. The authors plotted the liquidus surface of the ternary
5yatem on the basis of thermal analysis data of three binary systems
formed by the compounds, and of the three polythermal cross sections of
the ternary system. The liquidus surface.consists of a field of primary
crystallization of continuous, ternary solid metallide solution of the
system Ni3Nb + Ni 3Ta + Ni3Ti. Microstructural analyses of cast and
annealed alloys confirm the existence of solid solutions in the ternary
system. Fig. 6a shows the cast (mostly dendritic) structure of the
Card 2/a

89906
S/062/61/000/002/001/012
Equilibrium ofthe ternary system B115/B207
alloy: 1YA Ni3 Nb, i5~i N13 Tag and 70% Ni3Ti. Fig. 6b - of the alloy:
17% N13Nbt 33% N13 Ti, 50% N13 Ta., and Pig. 6c - of the alloy:
12% Ni Nb, 7V1-Ni Ta, 18% Ni Ti. 'The microetructure of alloys of the
3 3 , 3
same composition has become polyhe'dral after annealing at 12000C for
24 hr (Figs. 6dv e, f). Finally, 'the authors studied the hardness in
the cast and the annealed state. The table shows the results of measure-
ments of polythermal cross sections. Not only microstructure, but also
hardness confirm the data of thermal analysis on the existence of
continuous, solid solutions of metallides in the ternary system.
There are 7 figures, 1 table, and 7 Soviet-bloc references.
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov, Academy of
Sciences USSR)
SUBMITTED: ~October 2, 1959

28873
1%04 s/ift/61/ooo/oWoil/020
E021/E580
AUTHORS: Kornilov, I.I. and Polyakova, R.S. (Moscow)
TITLE6. Study of the properties of titanium-vanadium-
molybdenum alloys
FERIODICALt Akademiya nauk SSSR. Izvestiya. Otdeleniye teklitiielies-
kikh nauk. Metallurgiya i toplivo, 1961, No.1f,
PP 76-82 + I plate
TEXT: The Ti-V-Mo system was studied by microstructxiral
and X-ray analysis, and hardness, electrical resistance and high
temperature strength measurements. Alloys were studied along
quasi-binary sections with constant vanadium contents of JO, 204
30, 46, 50, 6o, 70 and 80 wt.%. The initial materials had
purities of Ti - 99.6%, V - 99.2% and Mo - 99.9%, Alloys were
prepared by melting in an are furnace using a non-consumr-b*Le
electrode, and by sintering powdered mater3.alm. In the (Inenched
state, the alloys consisted of a homogeneous solid solution hused
on 0-titanium. In the annealed state, Ti rich alloys showed all
acicular structure of two phases (a + P) whereas alloys rich xin
Mo and V had the polyhedral structure of a solid solution. All
alloys with 40-80% V had a homogeneous structure. X-ray analysis
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213873
Study of the properties of ... S/lOo/ki/ooo/ooli/oiL/020
E021/E580
confirmed the metallographic e'xaminiation and showed that the
transition from a single phase to a two-phased region cLctirrefd
between 70 and 75% Ti. Fig.4 shows the hardness and eiol-kr%,.~cil
resistance of alloys. The highest hardness values were.
in alloys containing 10, 20 and 30% V. in the region of the p-solid
solution. High temperature strength was measured by th 12 centri-
fugal method with a constant bending stress of 15 kg/irtm ot ~-009
550, 6oo, 650 and 7000C. The highest values were obtaired with
alloys consisting of P-solid solution, with V contents of* .111, 20
and 30%. On the basis of the microstructural and X-ray analysis.,
isothermal sections of the phase diagram were constructed fo-,
room temperature (Fig.6) and for 1100% (concentrations in
There are 6 figures and 5 references.- 3 Soviet and 2 non-Soviet.
The English-language references read as followst Ref.2t Taylor,J.L.
Beta Phase Parameters in the System Ti-V-Mo,, J. Metalal 1956, '8'
No.8, Sec.2, 956-961; Ref-3t Adenstedt, H., Reqignot J.,
Raymer, J. The titanium-vanadium system. Trans. Amer. Soc. Metals,
1952, 44, 990. N. 1. Davydov participated in the experiments,
SUBMITTED: April, 1961
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33181
S/18o/61/ooo/006/015/020
00 E193/E383
AUTHOR: Kornilov, I.I. (Moscow)
TITLE: High-temperature strength of intermetallic compounds
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye
tekhnicheskikh nauk. Metallurgiya i toplivo,
no. 6, 1961, 130 - 136
TEXT: it is pointed out,in a general discussion of high-
temperature strength of intermetallic compounds and alloys based
on such compounds, that thermal stability of intermetallic
compounds is determined by the strength of interatomic bonds
which, in turn, depends on the difference between the chemical
nature of the interaciing component. All metallic compounds have
a hardness and strength higher than that of the respective pure
metals or solid solutions and they retain these properties at
temperatures higher than their components. Among the large
number (about 4 000) of intermetallic compounds, Ni 3Al is
distinguished by high strength combined with a relatively high
ductility. The high-temperature strength of this compound.can be
further increased by alloying it with elements (Co, Cu, Fe, Cr,
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33181
s/18.o/61/000/006/015/020
High-temperature strength .... E193/E383
Mo, Ti, Si, V and Mn) with which it can form a limited series
of solid solutions. Similarly, intermetallic compounds Ti6 Al,
Ti3Al and TiAl alone, or alloyed with other metals, have a
high-temperature strength superior to tbiat of pure Ti. The
discussion is illustrated by experimental data quoted from
American, British and Soviet sources, the latter including
earlier worlis of the present author. Typical of these are data
reproduced in Fig. 5 (Ref. 21 - the author and Ye.N. Pylayeva
Zh. neorganich. khim. 1958, no. 3~ 673), where the deformation
(f, mm) of various test.pieces tested for creep under a bending
stress of 6 kg/mm 2 at 800, 900 and 1 030 0C (graphs a, 6 and B,
respectively) is plotted against time (-%L, hours), Curves 1-6
relating to pure Ni (1) and to Ni-base solid solutions containing
Nb (2), Ta (3), Ni Ti (4), Ni Nb (5) and-Ni Ta (6).
3 3 3
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33281
High-ternpe~aturd:strength .... E193/E383
There are 7 figuresand 24 references:, A Soviet-bloc and
6 non-Sovict-bloc. The four latest English-langtiage reference!3
mentioned are, Ref. 10: Nat. Phys. Lab,., 1959, v. 1, 111
Ref. 12 --J. Westbrook: Mechanical properties of intermetallic
compounds. John Wiley and Sons, USA, 1960; Ref. 19: R.W.
Guard, J.H. Westbrook.- Trans. Met.Soc. AIME, 1959, Oct.v.215,
no. 5, p. 807; -Ref. 20: M. Elansen - Constitution of Binary
Alloys. McGraw-Hill Book Co., New York, 1958.
SUBMITTED: April 26, ig6i
Card

34523
S/659/61/007/000/010/044
18.1-00 'D217/D303
AUTHORS: K #1-p and Snetkovp A.Yao
TITLE: Lattice parameters of the terminal solid solutions of
certain elements in nickel
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Iseledova-
niya po zharoprochnym splavanp va 7, 19619 106 - 111
TEXT: The results of an investigation of the influence of Mo, Nb,
Ta, V, Ru, W and Zr on the change in lattice parameter of nickel
when these elements dissolve in it, is reported. Most of the alloys
were prepared in a vacuum furnace. Ni-Ta alloys were prepared by Ye.
N. Pylayevaq Ni-W and Ni-Mo alloys by N.T. Domotenko, and Ni-Ru, Ni
-Nb and Ni-Zr-,alloys by K.P. Myasnikova. The above workers investi-
gated the equilibrium diagrams and properties of the alloys of the
respective systems. Powders or filings of the alloys were subjected
to X-ray photography. Prior to exposure, specimen lumps of the al-
loys were first homogenized at 1100 - 1150uC for 100 - 150 hours,
transformed into powder and sealed into evacuated quartz ampoules.
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S/659/61/007/000/010/044
Lattice parameters of the terminal ... D217/D303
The latter were annealed at the required temperatures for periods
of time sufficient to ensure equilibriump and then cooled in water.
After heat treatmentg one portion of the filings was submitted to
chemical analysis, and the rest sifted through a 200 mesh sieve and
mounted in the camera for exposure. X-ray exposuress, were taken in
back-reflection cameras using OuKa-irradiationp the distance bet~wen
the specimen and the film being 75 mma The temperaturey at which
the pictures were taken was 21 � 1.50C, the total error in measur.-
ing the lattice parameter without correction for temperature being
0.0006 - 0.0009 KX. It was found that the change in lattice parame-
ter of nickel on dissolving various elements in it depends on the
position of these elements in the periodic system and on their ato-
mic diametersp i.e. it follows the same laws as those which deter-
mine the limiting concentration of partly soluble metals in nickelo
Elements having the same type of crystal lattice (body centered cu-
bic) owe their influence mainly to their atomic diameterv even
though they may belong to different groups and periods of the perio-
dic table. The strengthening effect of an element is the greater
the greater the extent to whichg on dissolving in nickel, it increa-
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