SCIENTIFIC ABSTRACT PSAREV, V. I. - PSCHERA, J.

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• Collection: Scientific Abstracts
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• Sequence Number: 3
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

137-58-2-2809
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, N-r 2, p 87 (USSR)
AUTHORS. Kurilekh, D. G., Psarev, V. '1,
TITLE- The Nature of the Drop in Yield Point in the Finishing of Sheet
Steel (0 prirode ponizheniya predela tekuchesti pri otdelke
stal I nykh listov)
PERIODICAL: Nauchn. zap. Dnepropetr. un-ta, 1956, Vol 45, pp 69-71
ABSTRACT: A study was made of the mechanical properties of annealed,
and leveled sheet steel, and an attempt was made to determine
the cause of the drop in the rrc value after leveling. Used in
the tests were sheets of steel 08KP, annealed at 680-7101 for
8 hours - The sheets, 2000-2500 mm in length, were cut in
half. From the one half samples were cut to be tensile-tested
to destruction at angles to the direction of rolling of 0, 30, 45,
60, and 900; the other half was sent on for leveling, then for
mechanical testing. Reduction amounted to 0 - 85-1. 0 percent.
Tested were 6 sheets, 120 samples; the thickness of the
samples was 0.82 mm. Chemical composition and test-result
tables are included. The penetration depth of the leveling de-
Card 1/2 formation was studied by X-ray. It was found that the solid

13 7- 58- 2 - 2809
The Nature of the Drop in Yield Point (cont
background of the line (110) receded from the surface to a depth of up to
0. 05-0. 07 mm in sheets reduced by 1. 0 percent, and to a depth of up to
0. 08-0. 12 nim in sheets reduced by 1. 8 percent. In the leveled sheets the
(7s value dropped from 24.05-26.7 kg/mm?- to 19-35-2075 kg/mm?, with a
different value for each direction tested. Changes in Cyand were insig-
nificant. It is assumed that the increase in the surface area of a sheet re-
sulting from a plastic flow of the ferrite grains in the surface layers of the
sheet should lead to an elastic deformation of the individual grains not only
on the surface but throughout the thickness of the sheet. The effect of level-
ing on the sheet steel was such that the elastic tensile deformation of the
inner ferrite grains was balanced out by the elastic compression deforma-
tion of the surface layers. When the samples were tensile-tested, the pre-
existing elastic deformation of the grains was made evident by its absorp-
tion of sorne of the stress --- which was apparent from the drop ;in the (7s
va lue
D. M.
1. Sheets-Properties 2. Sheets--Steel-Analysis
Card Z/,_'

002/022/033
AUTHOR: Psarev, V.I.
TITLE.: Coagulation of the carbide phase dur:Lng tempering o:C
a molybdenum steel
1-1PRIODICAL: Fizilca metallov i m etallovedeniye, v. 15,, no.. 2 i 1963,
234-238
'T: has b en
~TEX The coagulation of carbides e studied in tWo*
molybdenum steels: 1) 0 - 0 40f; C, 0.34 Din, -0-17 Si, 1.39 Mo and
2) 1. 27% C, o. 4 6 DI-n, 0. 2 1 S i and 1.04 Mo. -, Specimens with a
suitable carbide structure were-s.elected.from batches tempered at
.the
600 9C. Coagulation-was studied at 600, 650. and 700 *C by
microscopical examination of specimeps-after quenching and surface-w.:
stripping. Coagulation during-continuous-'heating at 10, 50 and-
100 OC/hour was also studied cr- steel .(I). Crystal-structure
changes wer-e studied by X-ray diffraction on carbides isolated
electrolytically, the structure obtained under the test condItIon-s
beln- that of cementite.. Redistribution of molybdenum -,between the'l.,
crystal lattices of alpha-iron and. cementite -leads to breaks on-~
the curves correlating average -carbide-particle radius and
Card 1/3

J,
S/126/63/015/002/012/033,~
Coagulation of the carbide phase...
E111IL151
'65 C; at.70(
isothermal holdin time at 600 and 0 *C coagulation.
dies away, virtually ceasing ~.fterabout- 80 hours, The. hardness.
changes correspond' . to the changes in, the dispersion- of. the
carbide phase and in the state of the alpha-solid,solution.
Comparison of these results and those with-carbon steel indicate
s n ase and
that molybdenum. increases the disper io ofthe carbide ph,
at the same time greatly retards the coagulation. Theresults show"
that carbide coagulation is governed.,by diffusion of carbon, but
also that the state of the matvlx crystal lattice greatly, affects
both the dispersion of the carbide.particles and their coagulation.
The kno-rrn fact that alloying stee 1- with a very smal 1: amount of Mo.
does not lead to a large.change in the carbon diffusion.coefficient..
althoul-h the carbide phase.~is considerably more dispersed and the"
carbide coagulation parameters.greatly ahanged,.is explicable in.
terms of the,equilibrium co'nditions.in a :simpl~lf ied model. Similar.
results should be obtained with steels alloyed-with other carbide.-
forming elements in quantities insufficient to form.speclal
,-carbides.
There are 4 figures and 1 table.
ar
C
d 2/3

PSAREV, V.I.; MAKOVIYCHUK, Yu.I.; STEFANOVSKAYA, N.D.
Coagulation of the carbide phase in molybdenum and vanadium
steels-at temperatures 1wer than the Al point. Izv
uaheb. zav.; chern. met. 6 no.8:120-127 163. ~KvYRA9*16:11)
1. Chernovitskiy gosudarstvennyy universitet.

...... ...
ACCESSION NR: AR4014151 S/0137/63/000/012/IO34/IO34.
SOURCEt RZh. Metallurgiya, Abs. 121211
AUMORt Psarevp Vo Io3 Galichukp Yao Do; Dobrv*dent,, Ka Ae
TIVEs On the intergrowth of crystals of the compounds CdSb and Zn3Sb2 in
alloys
CITED SOURM Nauchn. yazhegodnik za 1959 go Chernovitsk. un-to Piz~-xatema
fak. Chernovtsy*l 196os 617-619
TOPIC TAGSs Cadmium antimonide crystal, Zinc antimonide,crystal, crystal
aggregation, crystal intergrowth, centrifugal crystallization
TRANSLATIONi An investigation was made into the feasibility of consolidating
crystals of CdSb and Zn
3Sb2 in binary alloys of Cd with 25%*Sb and Zn with 35%
5b by the mechanical eflect of centrifugal forces on a crystallizing casting.
The alloys were prepared from c.p. Zn,, Sb of grade Su-Op and Cd of grade Kd-O,,
further purified by triple vacuum distillation. The q ystallization was carried
Card 1/2

ACCESSION NR3 AR4o14151
out in evacu4ted pyrex ampoules, which were cooled together with the furnace
after the metal had melted, at rest and with rotation, During the rotatio4 and
in the c6urse of the solidification, the CdSb and Zn3Sb2 crystals, which differ
considerably in density from the adjoining liquids grow together into large
aggregates* This is illustrated by a comparison of the microstructures of the
specimens cooled with and without rotation. V. Zolotorev6kiy.
DATE ACQs o9jan64 SUB CODE.- ML, PH, CH ENCL.- 00
Card 2/2
'7f 1

KOSTUR) N.L.; PSAREV, V.I.
Methods of doPJLng the crystals of CdSb compounds through alloys of the
system Cd - Sb. Fiz. met. JL metalloved. 16 no.1:71-79 J1 163.
(MLRA 16:9)
1. Chernovitskdy gosudarstvennyy universitet.
Netal crystals) (Cadmium-antimony alloys)

FSARXV. T.I.
Methodology involved in heating and cooling according to a
previously given law, Inzho-fizozhur. no.1:98-102 Ja 160.
(MIRA 13:4)
1. Gosudaratvenny7 universitet, g.Chernovtoy.
(Furnaces)

BIYUMENFEELID, V.N.; LYLIFUR, S.L.; LIVSHITS, B.S.; PARILOV, V.P.;
V.Ye.; GOLUBTSOV, I.Ye., otv. red.;
KIaILLOV, L,I-',. red.; SLUTSKB-I, A.A., tekhn. red.
[1-Ifethodology for designing the equipment of crossbar automatic
telephone exchanges] Metodika rascheta oborudovaniia ATS koordi-
natnyk-h sistem; informatsionrjyi sbornik. Moskva, Gos. izd-vo
lit-ry po voprosam sviazi i radio, 1961. 130 P. (MIRA 15:4)
(Telephone, Automatic-Equipment and supplies)

AUTHOR: Psarev,.V. SOV/78-3-10-36/38
TITLE: Computation of the Line of Cementite-Austenite Equilibrium ir.
Fe-C Alloys (Raschet linii tsementitno-austenitnogo ravncves--Iya
Fe-C splavov)
PERIODICAL: Zhurnal necrganicheskoy khimii, 1958, Vol 3, Nr 9, pp 2217-2218
(USSR)
ABSTRACT: The paper under review is an attempt at computing the line of
cementite-austenite equilibrium in Fe-C alloys with consideration
to the mathematical dependqnce of the n-grain size of the Fe 3C
particle on temperature and concentration. The deper-aence of than
n-Erain size of the Fe 3C particle on temperature and concentration
is given in the equations 1 and 2:
r
r2 C
- C11
r, [n 0 (T T )+T 1n
17 a c 2- 1 1 c
Card 1/3

SOV/78-3-9-36/38
ComptitatJon of thc Line of Comeritito-Aunteni to Equilibrium in Fe-C Alloyn
r
r r 0 c (2)
0 i_ 0 T
(-a
In these equations r represents the n-grain size of the Fe 3 G
particle at the temperature Tif Z' 2 the medium grain size of
Fe3 C at T2, and c2 the respective concentratiorn at the limits of
the particle with the radii r I and r2-
The above formulae were tested in numerous experiments with
highly disperse Fe-C alloys. The dependence obtained between the
solubility of the compound Fe 3C at different temperatures is
used for the computation of carbon concentrations in Fe-C system!i.
There are 2 tables and 3 references, 3 of which are Soviet.
ASSOCIATION: Chernovitskiy gosudarstvennyy universitet (Chernovtsy State
University)
Card 2/3

.-IOTH01i llsarc-"' V-1, SOV-21-53-1-11/29
TTTLE: Comr)utation of the Activation Enerjy wf the 77a-rbide Criagul -
ation Process in Steel f%Ras,;hgt energili aktivats,-i prot-sessa,
koagulyallsii karbidov v stali)
PERIODICAL Dopovidi Akademii nauk Ukrainslkoi RSR, 1958; Dr 4"
PP 386-389 (USSR)
ABSTRACT: The diffusion character of coagulation of various fine-dis-
persed carbide particles in ste-21s makes it possible to cal-
culate the activation energy of this process, The euthor
derives a formula for this activation energy.-
V,

T,
are two
where R is a universal gas constant; v
and v
1
2
values of the linear growth rate for temperatures T I and
T2 at the same size of the particles. The author carried out
exDerimental investigations for a series of carbon steels,
Ir
om 1.2 to 1.7% C, at a wide range of temperatures, from
750 to 9500C, and treated the results by the least-square
Card 112 method, The final result was 32,000 cal/g-at, and the

SOV-21-58-4-7/29
Computation of the _!ctivation Energy of the Carbide Coagulation Process
in Steel
activation energy (above the critical point A,) closely
agreed with that of carbon diffusion in austehite determ-
ined by M.Ye. Blanter f-Ref. 2_7 and others. Similar com-
putations were also performed by the author for various
steel alloys. There is 1 graph and 5 references, 4 of
which are Soviet and 1 American.
ASSOCIATION: Dnepropetrovskiy gosudarstvennyy universitet (Dneprope-
trovsk State University)
PRESENTED: By Member of the AS UkrSSR, V.N. Svechnikov
SUBTV'ITTED: July 5, 1957
NOTE: Russian title and Russian names of individuals and insti-
tutions appearing in this article have been used in the
transliteration.
1. Carbides--Dif-Lusion 2. Diflousion--Mathematical analysis
3. Steel
Card 2/2

S/l4k$/62/000/0l2/OE)3juo8
E07JL/El5i
AUTtIORS Psa re v,.' VO If and: Kurobiy. 0. 1.
T IT LE: Infiu.ence of the*.state of the solid solution on the
kinetics of -coagulation and dispersion of the carbide
phase in 'steels
PERIODICAL: Izves .ti.y.avysshikh uchebnykh zave'deniyo 'Chernaya
Meta-llurgiya, do.-12.' 1962, 103._~ 109
TLX.r: The influerice of the state of the.matrix phase, the
groin boundaries.and of -grain size -ou the '_66ogulation .-of -carbides; -
was investigated.for-the st,eels' LL) X 15 (ShKhl5,) '(1:0 IM- C, i.5y;*.Cr,
u. 44to- Vn) \1 17 (U-17) (1.-6751, C),.,'and ~Vor,a nickel Stee'l (I. 175a Ce
AL.. 5,'.. Ni) -made- from - Armco- :iron in a high frequency furnace in -argon
atillosphere'. rhe..'s-pec-itn4ens were water-qM Ie.Rictied -from-. 1100 OC%
an..nea.1.ed.- at - 620-650 "..C 'And''xiven isothermal treatm,en .to at various
.tempexa tu res *,*, itt add i.tion they'were re,heated-and quenched from
varl Ious. temp,rira tvres -between -950 and 1150 0 c.. from the number.'and
tueAn radii of the carbide particIes, calculations wer.e. made of the
liue~ar velocity of their growth and of ~thel~ ,two parameters- of the
codgialation procesla: parameter characterIsIng the slowing,
card',1/3

S/148/bZ/OW/0121003/008
Influence of1the**3t&te of the solid...
,down of the. coagulatio .n in the later 'stages of the process;. and
P. - parameter chara.cterislng the acceleration *of the' coagulation
in the early stag6s. 'It was shown that the' velocity 'of
cdagulatigne t.h,e' 46~gree of -dispersion of the carbide phase and the
degree of slowing down,of the process largely depend on the state
of the. (x and solid solutions. The' higher-the.hardening
temperature, Ahe.larger will be the grain, size 'ofthe solid
soiu ,fion, -the more dispersed -will he the carbide'-pha .se 'and. the
higher will be the hard.nessi of the steel throughout the course of
-the coagulation proceso and vice verma. The.-.valueb of parameter 0
are higherfox..speciuiens hardened from 'lower tem~peratures,'an_d -
those of are- higher for 8pecimens 'hardened 'frona
higher tentperatureab .--Conclusions; 7 -:th*. procesi of Cioagulation of
carbides along gra'ih boundaries and o.ther weak places- is
determined not,onl-~,by the.-diffusIon coefficient,. but al:so,by*-.-
Y
changes 'in, the* solid. solution, it is necessary to conisider-the
influenc~e of'ah alloying element on the.state of the matrix,of
the solid solution, (,bond.forces presence of defects, grain gize-s
etc) as well as an chdriges,of the,latter.(intensity of healing-
Card 2/3

Influence of the state of the solid... s/148/b2/000/012/003/008
E071/E151
of lattice defects, mobility of matrix grain boundaries, etc)
during the process of heating.
There are 5 figures and 1 table.
ASSOCIATION: Chernovitskiy gosudarstvennyy itniversitet
(Chernovitsy State University)
SUBMITTED: January 23, 19b2
Card 3/3

FSAREV, V.I.; SALLI, I.V.
--- Coalescence of finely dispersed particles and determining surface
tension on solid phase boundaries. Fiz. met. i metalloved 5 no.2:
268-278 157. (MIRA 11:3)
l.Dnepropetrovskiy gosudarstvennyy universitet.
(Surface tension) (Alloys--Metallography)

AUTHORS: Psarev, V. I., and Salli, I. V.
126-2-12/35
TITLE: Coalescence of finely dispersed particles and determination
of the surface tension at the boundary of solid phases.
(Koalestsentsiya melkodispersnykh chastits i opredeleniye
poverkhnostnogo natyazheniya na granitse tverdykh faz).
PERIODICAL: Fizika Metallov I Metallovedeniye, 1957, Vol. 5, No. 2,
pp. 268-278 (USSR)
ABSTRACT: Coalescence is a process of coarsening of the particles
(grains or crystals) of the disperse phase brought about by
displacement of matter from the small particles to the larger
ones. This process is of great importance during tempering
of hardened steels, during heat treatment of etching alloys,
etc. An attempt to describe quantitatively this process has
been made in earlier work of the authors of this paper and
also of other authors (Refs. 4-7,9). It Is known from thermo-
dynamics that, in the case of coalescence, the change in the
free energy of the system AF is proportional to the change
of the total surface of division between the phases and AF
8 As, whereby the coefficient Crrepresents the specific free
energy on the surface of division of two phases. Thefunda-
Card 1/7 mental relations of the molecular-kinetic theory of phase

126-2-12/~;~5
Coalescence of finely disperst~d particles and determinati3n oFthe
surface tension at the boundary of solid phases.
transformations include this important thermodynamic
maunitude but so 'Lar no reliable data are available even
oil the order of maGnitude of a for solid phase
boundaries. In this paDer a calculation is presented
with the aim of determinin.- the order of maE;nitude of
the surface tension at the boundary of the solid phases
usinG experimental data on the kinetics of coalescence.
During coalescence all the particles of the disperse
phase can be sub-divided into the following two classes:
large, growing paxticles, i.e., particles which continue
to -row all the time until the process is stopped;
dissolving particles, i.e. smaller particles, the smallest
of which dissolve during -~~ie first stages of coalescence
whilst the larger ones may even grow in the initial stage
and still dissolve late--. Bokshteyn, S. Z. (Ref.3) has
found that during coalescence the average dimensions of
the particles of both classes increase all the time.
Konobeyevskiy, S. T. (Ref.1) proposed a formula for the
Erowth of the average particle size of the disperse phase
as a function of time during isothermal annealing in which
Card 2/7 the rate of growth is expressed by a linear relation; for

126-2-12/35
Coalescence of finely dispersed particles and determination of the
surface tension at the boundary of solid phases.
a better agreement between this formula and the experi-
mental results, the authors of this paper introduce a
decelerating term of the rate of growth thus obtaining
Eq.(l), p.269. The deviation of the coaGulatinF system
from the equilibrium position can be characterized by a
linear speed of Growth of the average dimension of
coarsening particles at a given instant of time. However,
with the progress of time the particles grow big.-er and
the speed of growth will decrease and tend to become zeio
In earlier viork of one of the authors (Ref.7), a iormula
was proposed for calculating the average dimension of the
particles which contains a term with an exponential
deDendence on time. An equation is also derived for
calculating the surface tension c at the boundary of
solid phases, Eq.(7), p.271. If e-~:perimental data are
available enabling plotting the dependence of the
average radius of the disperse phase particles on the
duration of isothermal annealing (Fig.1, P.70), it is
possible on the basis of the here derived relation to
evaluate the surface tension at the boundary of solid
Card 3/7 phases. For verifying the proposed formula the authors

126-2-12/35
Coalescence of finely dispersed particles and determination of the
surface tension at the boundary of solid phases.
used the experimental data of Bokshteyn , S.Z. (Ref-3),
Schimura, S. et alii (Ref.8); the basic data extracted
from the experimental results of these authors, which
are necessary for calculating the surface tension, are
entered in Table 1, p.272. In addition, the method of
calculation is verified on extensive exDerimental data
which permit-s determining the surface tension at the
boundaries graphite-austenite, carbide-austenite and
carbide-ferrite. The process of coalescence of graphite
Darticles in iron was investigated on two groups of
specimens, the first consisting of iron with a nearly
eutectoidal content of admixtures, i.e, 19- Si, 0.3% Un,
0.15~1o' P and 0.1% S, the second was prepared from pure
synthetic iron with the same C and Si contents as
for the first 6roup but having a minimum content of the
other admixtures. The experimental technique was
described in an earlier paper (Ref.6). Tables 2 and 3
Give the data on the dependence of the numbers of grains
-oer unit of volume on the time and temperature of
annealing of various specimens of malleable iron. The
Card 4/7results are entered into tables and they are discussed

126-2-12/3~
Coalescence of finely dispersed particles and determination of the
surface tension at the boundary of solid phases.
in some detail. The data contained in the paper justify
0 u
the assumption that the presented method for determining
the order of masnitude of surface tension at the boundary
of the solid phases is fully satisfactory and this view is
supported by a number of facts. The same value was
obtained for the surface tension of cementite at the
boundary with ferrite by determininG it from t ee
different sources. For the steel Y-8 at 65PCr 0
cr = 15 dyn/cm, for beloiv-eutectoidal steel at 630 0
Bokshteyn (Ref-3) obtained a = 13.2 dyn/cm. 0 whilst for
steels with various carbon contents at 720 C Schimura
et alii (Ref.8) quoted the value cr = 7.5 dyn/cm. If the
temperature is taken into consideration these values can
be considered as being fully in agreement. According to
Schimura et alii (Ref.8) the surface tension of cementite
at the bounda:r-y vilth ferr:Lte remaIns constant when
changing the carbon concentration. For all the investi-
gated alloys the magnitude of the surface tension decreases
with increasing -temperature, whereby the decrease is
almost inversely proportional with the solubility of the
Card 5/7 disperse phase in the T:1other phase (in the temperature

126-2-12/35
Coalescence of finely dispersed particles and determination of the
surface tension at the boundary of solid phases.
range where no phase transformations occur). The surface
tension of cementite at the boundary with austenite is
almost five times lower than the surface tension of
graphite at the boundary mrith austenite. This fact is
confirmed by phenomena which accompany solidification of
iron. InvestiGation of alloy steels showed that for a
relatively small content of -the alloying element, of the
order of 2yo, the order of magnitude of the surface
tension does not change. However, a definite tendency
towards increasin- can be observed i n the surface tension
of carbide bounding on ferrite on introducing carbide
forming elements (Cr,Ti) emd a tendency can be observed
towards lowering of the surface tension on introducing
non-carbide forming elements? cobalt for instance. The
obtained values of suvface tension appear reasonable also
as regards the determined size of the critical
germination nucleus durine; phase transformation, for
in8tance for steel containing 1.2% C and super-cooled to
50 C below the A, point, thg critical size of the
cementite germ is about 10-( cm, which is a fully
Card 6/7 realistic value for such -Lmdercooling.

126-2-12/35
Coalescence of fine.1y dispersed particles and determination of the
surface tension at the boundary of solid phases.
There are 4 figures, 10 tables and 10 references, 8 of
which are Slavic.
SUBMITTED: October 11, 1955 (Initially), April 10, 1957 (after
revision.)
ASSOCIATION: Dnepropetrovsk State University.
(Dnepropetrovskiy Gosudarstvennyy Universitet).
AVAILABLE: Library of Congress.
Card 7/7

;V,
_ ~;Yqu,, - V.I.
StreDgthening of crystals of chemical compounds in alloys of the
systems Zn - Sb, Cd - Sb, In - Sb. Kriatallografiia 5 no-3:
479-481 My--,Te 160. (MIR-6, 13: 8)
1. Ghernovitskiy gosudarstvannyy universitet.
(Zinc antimouide)
(Caclmium antimonide)
(Indium antimonide)

PSARzV, v. i.
'I On Caluulation of Kinetics Curves of Heating and Cooling.:
Report submitted for the Conference on Heat and Mass Transfer, Minsk,
BSSR, june 1961.

S/M/60/005/03/00/oO
AUTHOR: