SCIENTIFIC ABSTRACT UTEVSKIY, L.M. - UTEY, N.I.

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• Collection: Scientific Abstracts
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• Document Creation Date: November 2, 2016
• Document Release Date: April 3, 2001
• Sequence Number: 1
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

SOV/180-59-3-24/43
AUTHORS: Orlov, L.G. and Uteva:ziyj L.M. (Moscow)
TITLE: The Differences in Carbide Formation at Grain
Boundaries and within the Grains of a Quenched Steel
During Tempering
,~Z~RlODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekiinicheskikh
nauk, Metallurglya 1 toplivo, 1959, Nr 3, PP 132-134(USSR)
ABSTRACT; The steel 2OKh2N2 containing 0.2% C. 2~; Cr and 2% Ni was
investigated. An electronmicrograph is shown in Fig Ia.
It can be seen that the size and shape of the particles
in the grain boundaries and within the grains are
different. The chemical composition was determined by
microdiffraction in the electron microscope. Th e
electronnticrograph and the diffraction pattern of the
particle at the grain boundary are s1hown in Fig lb and 1C
ind an electroamicrograph of particles within the grains
in Fig 2. The particle in t1te grairL boundary (after
heatin� for 75 hours at 5GOOC) was Cr7C3 * After heating
at 650 C for '- hours however, particles of (CrsFe)- ,7C3
were detected. For these to form, diffusion of' buti,
Card 1/2 carbon and chromium is necessary. No enriching of' the

sov/180-59-3-24/43
The Differences in Carbide Formation at Grain Boundaries and
Within the Grains of a Quenched 5teel During Tempering
surface layers of the grains by chromium was detected.
There are 2 figures and 7 references, I of which is
English and 6 Soviet.
ASSOCIATION: Institut metallovedeniya i fiziki metallov TsNIIChM
(Institute of Metals Technology and Metal Physics,TsNllChM)
SUBMITTED: March 26, 1959
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UTEVS-'IIY, L.A., kand.tekhr..nauk
Some problems in the use of the semidirect method of alactron
microscopy for tho study of multiphaae alloys. Probl.natallWed.
t fiz.met, no.6:381-38,9 '59. O(M 12: 8)
(Blectron microscopy) (Alloys--Motallography)

S/137/62-/000/005/018/150
A0061AI01
AUTHORS: Spasskiy, M. N., Utevskiy, L. M.
TITLE: High-frequency vacuum melting furnace
PERIODICAL: Referativnyy zhurnal, Metallurgiya, no. 5, 1962, 52, abstract 5V309
("Sb. tr. In-t metalloved. i fiz. metallov Tsentr. n.-i. In-ta
chernoy metallurgii", 1959, v. 6, 520 - 526)
TEXT: A description is given of a new design of a high-frequency vacuum
melting furnace and its operation during one year. The melting time in the fur-
nace is 40 - 60 min. The main characteristic feature in the furnace design is
the method of fixing a double-wall water-cooled quartz tube and the installation
of the crucible and the mold in it. To prepare the furnace for the heat, the
quartz tube is not to be removed. The vacuum system, consisting of a diffusion
(H I 10-4mm
-5) and forevacuum (EH-1) pump. produces a pressure in the furnace of4r.,
Hg. The inductor displacement requires a minimum force. Thestopper device
ensures the necessary holding of the metal in liquid state and vacuum casting.
The furnace design ensures convenient and safe operation.
D. Kashayeva
rAbstracter's note: Complete translation]
L.
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16M SOV/32-25-4-24/71
AUTHORS; Yermanovich, N. A., Longinov, At. F., Orlov, L. G., Utevskiy, L.M.
TITLE: Examination of Interdendritic Nonmetallic Streaks in Cast 3-.eel
(Obnaruzheniye mezhdendritrLykh nemetallicheskikh prosloyek v
litoy stali)
PERIODICAL: Zavodskaya Laboratoriya, 1959, Vol 25, Nr 4, PP 440-442 (USSR)
ABSTRACT: Sites of fracture in some structural steels (40 KhNhtA, 12Kh2N4A,
30KhVFYu, 30 KhGSk, 30 KhGSNA) pointed to a destruction of the
metal along the boundary of the primary grain. On the strength
of tests it is assumed that nitrides, especially aluminum
nitride (I), accumulate at these boundaries and produce a
weakening. This assumption was examined in the present case by
means of an electron microscope and an electronograph. By an
ele--trolytic heating, a thin coating layer was obtained at the
site of fracture, which could be removed by the reagent ac-
cording to Popova and examined. On the microphotograph of a
fracture in the steel 40 KhNMA (Fig 1) one can well observe the
incluvions, the forms of which are reprusented even better by
the electron microscope (Fig 2). The phase composition of these
inclusions was investigated by the X-ray structure- and electro-
Card 1/2 nographic method. In the X-ray picture (I) was observed in the

SOV/32-25-4-24/71
Examination of Interdendritic Nonmetallic Streaks in Cast Steel
steel 38 KhVFYu (I), and (I) and VX in samples with big faults,
(I) and F3Al 2(S'04)3 in the steel 12 Kh2N4A - (I), and (I) in
the steel 40 KhNMA - (I). The electronograms (Fig 3 for 40KhNMA)
corresponded to a crystal lattice of (I). In order to convert
structural components from a disperse to a crystailine form, the
samples were treated in the vacuum (at 8000 for 2 hours)i a
fine formation of stains (Fig 4) was observed and the distinct
electronogram of a polycrystal (Fig 5) was obtainei with three
phases - a spinel lattice, (I) and a phase which could not be
identified. A test storing in the vacuum at room temperature
for some days showed a crystallization, the electron;gram of
which is described (Table). There are 5 figures and 1 table.
ASSOCIATION: Zlatoustovskiy metallurgicheskiy zavod, Tsentrallnyy nauchno-
issledovatellskiy inst-itut chernoy metallurgii (Zlatoust
Metallurgical Works, Central Scientific Research Institute of
Iron Metallurgy)
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9(7),18(7)
AUTHORSs Orlov-t L. G,t UteV3kiy, L. M. SOV132-25-9-211~3
TITLE: On the Ways of Investigating the Surface of Fractures by the
Aid of the Electron Ylicroscope
PERIODICAL: Zavodskaya. laboratoriya, 1959, Vol 25, Nr 9, pp 1084-1087 (USSR)
ABSTRACTs Electron microscopic investigations of fracture surfaces and
ground sections of metal can be carried out by directo indirect
and semi-direct methods (Ref 1). The possibility of investigating
the inter-crystalline fractures, the so-called micro-diffraction.
investigation, is particularly mentioned, and for this purpose
the domestic industry has begun a series production of the
electron microscopes EY,-5 and UEMB-100. The production of the
impressions is explained and some electron microphotographs(EM)
are given to illustrate characteristic bribtle and ductile
fractures of steel samples obtained during shook- and tensile
tests at different temperatures. The impressions were taken
with coal dust followed by separation of the carbon film
together with the inclusions with the reagent by N.M. PopoNa.
By means of the (EM) of a shearing surface of a steel low in
carbon (Fig 1) the so-called "river design" is explainad. The
Card 1/2 trans-crystalline corrosion of a tempered and drawn steel can

On the Ways of Investigating the Surface of SOV/32-25-9-21/53
Fractures by the Aid of the Electron Miefoscope
also take place along the surfaces of closely strewn carbide
deposits (Fig 2, steel 20Kh2N2) Micro-diffraction tests carried
out together-with N.M. Popova(on a 400 kv microscope of his
construction) showed that in brittle inter-crystalline
fractures in which the spillies run along the contours of the
carbide particles (Fig 4) the crystal lattice of these
particles on the whole remained unchanged after the fracture.
With the ductile fracture (Refs 15P 16) given in publications,
the failure crack occurs at the grain boundary (around larger
inclusions) as could be ascertained in the case under review
(Fig 5). The extent of the plastic deformation can also be
evaj.uated from the deformation type of the particles (Fig 6).
There are 6 figures and 16 references, 10 of which are Soviet.
ASSOCIATION: Teentrallnyy nauchno-issledovatellskiy inetitut chernoy
metallurgii (Central Scientific Research Institute for'Perrous
Metallurgy)
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PHASE I BOOK EXPLOITATION SOV/5412
Utevskiy, Lev Markovich
Otpusknaya khruokost' stali (Temper Brittleness of Steel) Moscow,
Metallurgizdat, 1961. 191 p. 4, 200 copies printed.
Ed. : R. I. Entin; Ed. of PuViishing House: Ye. N. Berlin; Tech. Ed.
Ye. B. Vaynshteyn.
PURPOSE: This book is intended for scientific workers and engineers in
physical metallurgy and may also be used by students in schools of higher
education.
COVERAGE: Fundamental experimental data on the phenomenon of reversible
temper brittleness of construetional alloyed steel are presented. Also
discussed are methods and results of the experimental research as well
as new concepts which have developed concerning the nature of thit: type
CArA;:.j-[-10-

Temper Brittleness of Steel
SOV/5412
of brittleness. The research methods which have been worked out may
be applied also to the solution of other problems in physical metallurgy,
particularly to those problems connected with processes occurring along
the grain boundaries. The experimental work was carried out in the
Laboratory for Phase Changes at the Institut metallovedeniya i fiziki
metallov TsNIIChM (Institute of Physical Metallurgy and Physics of
Metals at the Central Scientific Research Institute of Ferrous Metallurgy
im. 1. P. Bardin). The author thanks G. V. Kurdyumov, Academician,and
R.I. Entin, Professor, Doctor of Technical Sciences, for their assistance,
interest, and advice. He also thanks L. G. Orlov, Engineer, G. L. Ivano-
va, N. I. Kolltsova, Engineer, R. M. Koshelevskiy, Engineer, Ye. K.
Belova, Engineer, and A. I. Rizoll and L. G. Sakvarelidze, Candidates of
Technical Sciences, for their work in the experiments and investigations.
There are 240 references: 137 Soviet and 103 non-Soviet.
Card--2--/'Ig-

BAGARYATSKIYI Yuriy Aleksandrovich; GOLOVCHINER, lakov Mendelevich;
ILIINAq Vera AlekMevna; KAMISM t Emarmil Zellmanovich;
KARDONSM , Viktor Mikhaylovich; KRITSKAYA, Vladislava Kasimirovna;
LYSAKI- Leonid Ivanovich; OSIPIYAS, Yur:Ly Andreyevich; MW#
Mark Davydov-1ch; ROZEIMERG, Vladimir Moieeyevich; SANDLERt
Haum Isaakovich; TRAVINA9 Wadezbda Trofimo'vna) 17E-VSKZ#---
.TIAV uk_ovichL BERLIN, Ye.N., red.izd-va; VAYNSHTEYNt Ye.B.v
tekhn.red.
[Radiograpb;7 in metallograp1q] Rentgenografiia v fizicheskom
metallovedenii. Moskvag Goe,nauchno-tekhn.izd-vo lit-ry po cbernoi
I tavetnoi meta-Uurgiip 1961. 368 p. (KIRA 14:7)
(Metallograpby) (X-rays-Industrial applications)

- LITEVSKIY, L.M.t kand.tek3n.nauk
T(wper brittleness in steel. Keitalloved. i term. ob--.met.
no.605-41 Je 161. (HIPA 14:63
1. TSentrallnyy nauchnoiosledovatellskiy institut chernoy
metallurgii. (Steel-Brittleness)
(Tempering)
-*a-
I~i

100
29703
31-811611003101010351036
B125/B102
AUTHORS: Orlov, L. G., and Utevskiy, L. M.
TITLE: Electron microscopic observation of the motion of dislocatims
in alpha iron
PERIODICA-,: Fizika tverdogo tela, v. 3, no. lo, 1961, 3242 - 3246
TEXT: The present paper deals with an electron optical dark-field
observation of a 50t-thick alpha-iron foil out in parallel to thlE t1lij
plane (chemical composition: 0.013 C, 0-03 Si 1 0-04 Mn, 0.004 S, 0.002 P),
which was made with a Y311G-100 (UMB-100) electron microscope. An
accelerating voltage of 75 kv was applied. Stresses arising in the
electron-irradiated foil displace the dislocations in the thin film, and
characteristic contrast tracks are left over as a result. In an annealed
foil, dislocations are very difficult to displace by electron bombardment,
evidently due to the absence of free dislocations. The tracks caused by
the motion of dislocations, while looking roughly curvilinear, in reality
consist of straightlined segments. This change in direction of the tracks
is ascribed to dislocations which pass from one slip plane to another.
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29703
S/18i/61/003/010/035/0306
Electron microscopic observation... 13125/B102
The intersection between two slip planes, where screw dislocation passes
from one plane to another, is the projection of the direction of Buerger's
vector. The foil thickness was determined from the width.of the pro-
Jection of a known slip plane. It was found to be -1200 A. It was
experimentally proved that diBlocationa in iron also glide on planes of
the types 110~ andJ211?, and that they frequently pass over from one type
to the other by transverse gliding. There are 3 figures and 7 references:
2 Soviet and 5 non-Soviet. The three most recent references to English-
language publications read as follows: D. G. Brandon, J. Nutting. Journ,
Iron a. Steel Inst., .196, 2, 16o, ig6o; W. Cannington, K. F. Hale, D,
hie Lean. Proo. Roy. Soc., A 259, 1297, 203i 19601 B. Gale, K. F. Hale.
Brit. Journ. Appl. Phys., 12, no. 3, 1961.
ASSOCIATION: Inatitut metallovedeniya i fiziki metallov Moskva (Institute
of Metallography and Physics of Metals, Moscow)
SUBMITTED: June 28, 1961
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USIKOVI M.P.; UTEVSKIY, L.M.
Transfer of plastic defo=-ation by "relay." Fiz. met.imetalloved.11
no.6:952-954 Je 161. (MMA 14:6)
1. Institut metallovedeniya i fiziki metallov TSentrallnogo
nauchno-issledovatellskogo instituta chernoy metallurgii.
(Deform.ations (1-lechanics))

r 15 ~'D
S
0-0
S103 2119~
2/0/027/012/004/015
B104/B1O8
AUTHORS: Usikov, M. P., and Utevskiy,,L. M.
TITLE: Origin and interpretation of the contrast of an electron-
microscopic image of a metal foil
PERIODICAL: Zavodskaya laboratoriya, v. 27, no. 12, 1961, 1481 - 1466
TEXT: The production of the diffraction contrast in an electron-microscop-
ic image is studied. Pormulas for the amplitudes of electron waves
scattered by perfect and imperfect crystal lattices are derived on the
basis of non-Soviet bloc papers (D. Heidenreich. J. Appl. Phys., 20, 993
(1949); It. Katc. J. Sol. Japan, 7, 397 (1952); 8, 350 (1953); NI. J. Whelrn,
P. B. Hirsch. Phil. Mag., 2, 1121. (1957)1 M. J. Whelan. J. Inst. Metals,
87, 392 (1959); P. B. Hirsch, A. Howie, M. J. Whelan. Phil. Trans. Roy.
Sol. of London (A], 252, 499 (1960); H. Hashimoto, A. Howie, M. J. Whelan.
Phil. Mag., 5, 57, 967 (1960); G. Borrmann, Phys. Z., 42, 157 (1941); 127,
297 (1950)). The width of the image of a dislocation is estimated:
A x ~~ t' /n (t' = distance between two extinctions). The image of a thin
0
metal foil (Fig- 4) is interpreted. It is shown that for studying the
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21393
S/032/61/027/012/004/015
Origin and interpretation of the ... B4,00108
dislncation structure of a crystal specimen, sufficiently thin parts of it
may be used. As far as possible these partL; should be at some distance
from the edges of the foil. The properties of the individual dislocations
and their interactions and motions can, however, also be observed close to
the edges of the foil. It must also be borne in mind that some of the
dislocations and defects remain invisible. There are 5 figures and 9
references: 1 Soviet and 8 non-Soviet.
ASSOCIATIONt Tsentrallnyy nauchno-issledovatellskiy institut chernoy
metallurgii im. I. P. Bardina (Central Scientific Research
Institute of Ferrous Metallurgy imeni I. P. Bardin)
Fig. 4. Schematic representation of the image of a metal fail under an
electron microscope. Legend: (A) foil with the most essential defects;
(G) image of the foil; (1) - (6) variations in thickness and inclination
of the foil; (7) - (18) defects of the crystalline structure; (1) thickness
variation; (2) wedge-shaped end; (3) warping of the foil; (4) depression;
(5) pore; (6) hump; (7) defect of the crystal packing; (8) split disloca-
tions -aith packing defects of varying widths; (9) dislocation; (10) - (14)
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21393
S/032/61/027/012/004/015
Origin an([ interp re ta tion of the B104/B108
long dislocation, varlotu: nontr;vit effects; (10) ordinary dislocation;
(11 invisible dislocation-, (11) double imatre of a single dislocatiosL*,
(13~ ZiCZL,.' dislocation; (14) Jotted Image; (15) dislocation loops;
tetrahedral packing defect; (17) helical dislocation; (18) trace of
mirrating dislocation.
Fir- 4

7

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S/032/61/027/012/001-/Ol=
B104/BlOB
AUTHORS: Orlov, L. G., Usikov, M. P., and Utevakiy. L. M.
TITLE: Use of microdiffraction for the electron-microscopic
examination of metals
PERIODICAL: Zavodskaya laboratoriya, v. 27, no. 12, 1961, 1486 - 1490
TEXT: Structural analyses of small sections of metal foils can be con-
ducted with the adjustable elements of a modern electron microscope
(intermediate lens, variable aperture, and special microdiffraction
diaphragm). The method of these structural analyses is described. The
application of the microdiffraction method for various purposes is
demonstrated by several examples. New results are not given. G. S.
Zhdanov (Rentgenografiya metallov, ch. II., Gostekhizdat (1938)) is
mentioned. There are 5 figures and 6 references: 5 Soviet and 1 non-Soviet.
ASSOCIATION: Tsentrallnyy nauchno-issledovatel'skiy institut chernoy
metallurgii im. I. P. Bardina (Central Scientific Research
Institute of Ferrous Metallurgy imeni I. P. Bardin)
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IL
34843
S/129/62/000/003/004/009
E021/E335
AUTHORS - Usikov, M.F., Engineer and Utey4hiy. L-Al., Candidat(-
of Technical Sciences
TITLE~ Change in the dislocation structure of iXi8go-j
(lKhl8N9T) steel during hardening and softening
PERTODICAL: Metallovedeniye i termicheskaya obrabotka metalLov,
no- 3, 1962, 18 - 20 + 2 plates
TEXT~ Rolled samples, 0.04 nun thick were annealed in
evacuated vessels at 1 100 0C and deformed by 0.3 - 100%. Some
of the unannealed samples (with 960j-" deformation) were heated
at 4oo - 8oo oc for I hour. The strip was thinned after vario-~v~
treatments by electrolytic polishing in a mixture of 60c,,, 113PO4
and 40% 11 2504 at 2 - 4 A/cm2 current density and 60 0C. The
0
obtained 1 000 - 2 000 A thick foil was examined by an electron-
microscope. Dislocations show up because the distorted zone
along a dislocation has a strong scattering effect on the
electrons and the intensity of the beam decreases. Thus, dis-
ocati?3s show up as dark lines. It was founc' that the annealed
~
ar

s/i2q/62/ooo/oo5/oo!f/u,_,9
Change in the dislocatiori Ef)21/E335
material had only a low density of dislocat ions.. Ne (lisloc;%ttoii-,
were observed within the grains. Dislocations were seen oniy at
grain boundaries with small clegie.--es2of misor ent ation~ I'll e
density in the field of view ( 25 4 ) was 1.0 crtj _.
Plastic deformation of I% led to the appearance of dislocar Ion s
within the grain5~ The calculated dislocation density was
9 -,2
10 cm There was only one slip system in each grain. In
the case of deformation in excess of 1%, sl-ip on secondary svs,emQ-
occurred. Dislocations moving on different slip planes interc.ct
with one another and the material begins to har en.,_,.,Tlie di-s-
location density for 20,L deformation was X 1.0 Cm
Finally, deformations greater than 800 produced a large quantity
of dislocation networks; thick "clouds" of dlslocations were
observed inside the grains. A dislocation density of
10,10 cm-2 was observed after .101,1-0' deformation. I'll 1~ (I enS L t y 0
dislocations after cold-rolling (96o(0 was diff-i.cult to determine
12
but was obviously greater than .10 cm SoftenLng by heating
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5/129/62/000/003/oo4/oog
Change in the dislocation E021/E335
to temperatures below the beginning of recrystallization led to
no visible change in the positions and density of dislocations.
Recrystaiiization began at 625 0C and subgrains, fiee ft-om
dislocations and with sharp boundaries, developed, There were
no dislocations inside the grains at 700 0C and the structure
in this state differed from the annealed structure only in the
smaller grain size.
There are 5 figures,
ASSOCIATION-, TsNIIChM
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S/717 62/000/007/004/010
D207XT)303
AUT11ORSs Orlovo L.G.r and U ~did~te of Technical
Sciences
TITLE: Investigation of the micromechanism of the process of frac-
ture of steel and iron using the method of electron-micro-
scopic fractography
SOURCE: Dnepropetrovsk. Institut metallovedeniya i fiziki metallov.
Problemy metallovedeniya i fiziki metallovp no. 7P Moscowp
1962p 156 - 174
TEXT: The authors discuss briefly the techniques of electron-micro-
scopic study of the fracture surfaces. They also describe their own
results on iron and steel. Replicas were obtained by deposition of
carbon films on fracture surfaces which were then separated by elec-
trolytic etching or by using a reagent suggested by N M. Popova (Ref.
15: Karbidnyy analiz (Analysis of Carbides) Maohgizt ;949). The re-
plica micrographs (magnifications of 600 - 15POOO) were examined ip
a stereooomparator or with a stereomicrometer. In this way, quantita-
CW-d 1/2

S/71-1/62/000/007/004/010
Investigation of the micromechanism ... D207/D303
tive measurements of the surface relief were made. Reproductions of
replicas are given in the article. They are discussed for iron and
steels which suffered brittle fracture of transcrystalline (across
grains) and intercrystalline (along the grain boundaries) types. The
transcrystallire fracture occurred usually along cleavage planes and
the intercrystalline fracture was observed in samples with temper
writtlenass (obtained by quenchingp followed by 5000C tempering). The
authors reproduce also and discuss the ductile fracture surfaces in
iron and steol. There are 14 figures and 32 references: 13 Soviet-
bloc and 19 non-Soviet-bloc. The 4 most recent references to the Eng-
lish-language publications read as follows: 0. Crussard, R. Borioneq
J. Plateau, J. Morillon and F. Maratray, J. Iron and Steel Inst., 183
146 - 177P 1956; G.T. Hahn, 17-3. Owen# B.I. Averbachp and M. Cohen,
Welding J.? 389 91 1959; E. Wessel, J. Metalsp 9, 930, 1957; J. Wash-
burn, A.B. Gorump and E.R. Parker, Trans. Met. Soo. AIME, 2159 2P
1959-
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S/053/62/076/001/00;'/004
B117/B101
AUTHORSs Orlovt L. G., Usikovt M. P., Utevskiy, L. M.
TITLE: Electron-microccopic examination of dislocations in metalo
PERIODICAL: TJspekhi fizicheskikh nauk, v- 76, no. 1, 1962, 109 - 152
TEXT: This ia a survey on results achieved by applying electron micro-
soWy to the observation of dislocations in metals. Fii-st, the principles
of the investigat4on method are dealt with: Type of specimens to be used,
procedure of observation, electron-microscopic representation of defects
in crystalline structure, formation of diffraction contrasts. In the
to following, the principal results obtained as to the formation of disloca-
tions, their motion and interaction, structure of deformed metaland sohd-

.
So ification, dislocations and point defects, general and specific data as
c to the structure of thin foils are given. The authors point out that the
theory of dislocations and numerous predictions as to particular proper-
ties of defects have been confirmed experimentally during the last 5
years by using transmission beam microscopes for the direct examination
of the dislocation structure. In this connection, it is stressed that
ce.t.cl Card 1/2

UTEVSKIY,, L.M., kand.tekhn.nauk
Some consequences of the nonsi=Lltaneousness of supersaturated
solid solution decomposition JCnaide and along the boundaries cf
po2yorystalltne grains. Froblemetalloved. i f iz.met. no.7:198-
218 162. (MM 15:5)
(Alloya-lbtallography) (Nbt4 crystal)

AUMORS: Orlov, L. U., Utevskiy, L. M.
S11 37/62/000/0 12/024/085
Aoo6/Aic,i
TITLE: Studying the micromcchanism or the process of steel and Iron
failure by the method of electron-microscopic fractography
PIMIODICAL: ReferaLlvnyy zhurnal, Metallurgiya, no. 12, 1962, J46 -Arl, abstract
121277 ("3b. tr. In-t metalloved. I fiz. metallov 'Psentr. rt.-i.
in-ta chernoy metallurgli", 1962, v. 7, 156 - 174)
TaT. The method of electronic microfractography was usud to study brittle
and ductile fractures of Iron and steel specimens., To preserve a portion of the
carbide phase, elecLrolytic eLching and acparation of films in a special reactive
agent, were used. An analysis of the transcrystalline splinters in brittle fail-
ure of Fe revealed st"ps in the splinter which flow together to form one-larger
step. In brittle failure strong plastic deformations at the final stage of
breakdown take place be5ldes plastic deformation, preceding crack formation. The
deformation is sharply localized In the thin layer of the order of hundred3 and
even tens of Rngstroem. and forms a major part of the total plastic deformation
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3 /137/62/000/0 12102 It X35
Studying the microniechanism of the... Aoo6/Aiol
of the specimen prior to failure. During the Investigation of Lnterer7/stalline
fractures of structural alloyed steels in the state of temper brittlene.'j.5. it
is noted that cracks, propagating along the grain boundaries, spread around t 'he
outlines uf encountered carbide particles. The surface of.ductile fracLurus
consists of e!oncave cells. The final Btage of ductile failure Is characterizi-A
by a very strong, sharply localized, plastic flow, producing deformation:-, of
hundreds of percent; the particles of the second phase are then split into
halveb. Mere &re 32 references.
P. Zubarev
[Abstracter's note: Complete translation]
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S/126/62/013/005/009/031
Eogi/E435
AUTHORS: Usikov, M.P., Utevskiy, L.M.
TITLE: Change in the dislocation structure of nickel on
alloying with titanium, chromium and aluminium
PERIODICAL: Fizlka metallov i metallovedeniye, v.13, no.5, 1962,
701-709
TiXT: This is the first paper on systematic investigations of
the dislocation structure of nickel and its alloys, to establish
the fundamental influences of elements on the behaviour of
dislocations and on the nature of the dislocatian structures
forming during plastic deformation. Nickel and the following
alloys were melted in an induction furnace and cast into ingots
(composition, wt.%)
Card 1/4

S/126/62/013/005/009/031
Change in the dislocation E091/E435
Alloy Cr Ti L Al
XIA80 (KhN80) 19-70 -
HT4 (NT4) - 4.25
H ~O 4 (NYu4) - 4.15
I XH8oT2~O M.-MOT2YO 19.70 2.23 o.67
I X H 80T3 Q (KhN8OT3Yu) 19. 55 2.67 1.05
The ingots were forged to billets which were rolled, with
intermediate annealing, -own to a thickness-of 0.03 to 0.1 mm.
The strip obtained was-annealed in evacuated ampules at 10000C.
The specimens were cut into two portions, one of which was
deformed in tension to 0.5- 10% at room temperature; the other
portion of the Ni, KhN80, NT4 specimens was deformed in tension
in a special vacuum apparatus at approximately 50*C below the
recrystallization temperature of each alloy. The strips were
Card 2/4

S/126/'2/013/005/009/031
0
Change in the dislocation ... E091/E435
then thinned down to 500- 2000 X by means of electrolytic
polishing for inspection under an electron microscope. It was
found that there are virtually no dislocations within'the grains
of nickel and its alloys in the annealed state. However, even
in the early stages of work-hardening, dislocation networks form.
With inci-ease in the degree of deformation, a characteristic
cellular structure forms. The distribution of dislocations in
nickel changes radically by alloying it with titanium, chromium
and aluminium. The behaviour of dislocations in the binary
alloys KhX80, NT4 and NYu4 resembles that of dislocations in
stainless steel; their movement in the early stages of
deformation proceeds along strictly straight paths and, provided
the foil is sufficiently uniform in thickness, the dislocation
traces- always form perfectly straight bands. At above 10%
deformation, the structure of binary alloys becomes cellular.
The above differen;-,e between the dislocation structure of nickel
and its alloys is due to a decrease in the stacking fault energy
on alloying nickel. This increases the width of the stacking
fault, which hampers transv,.--rse ilip, i.e. the transition of
disloj!~ations from one ;Ylip plane to another. The dislocation
C-- rd '~"l

S/126/62/013/005/009/031
Change in the dislocation E091/E435
structure of the ternary alloys KhN80T2Yu and KhN80T3Yu, after
1 to Zo deformation followed by annealing at 1000*C with
subsequent air cooling, is similar to that of the binary alloys at.
the same degree of deformation. At higher degrees of deformation
however isolated regions with very high dislocation densities
become visible. The formation of dislocation is in-pairs,
associated with the ordering of the solid solution; the first
dislocation disturbs the order and the second restores it.
The disloc 'ation. structure of alloys deformed in tension at
elevated temperatures differs fundamentally from that obtained by
deformation at room temperature; no conglomeration of
dislocations occurs at elevated temperatures. There are
12 figures and 1 table.
ASSOCIATION: Institut metallovedenlya i fiziki metallov TsNIIChM
(Institute of Science of Metals and Physics of
Metals TsNIICh11,1)
SUBMITTED: july 14, 1961
Card 4/4

ORWO L.G,3 USINOV9 MrP.,* UTEVSKIYv L.M.
Obiservation of dislocations in metals by means of an electron
microscope, Uspo fis. nauk 76 zo.lA109-152 1& 162o
(MM 1582)
Dislocations In crystals)
eatron microscope)
M

$ __p -- M--
--- UTEVSKIY~-I. -K~-and-USIKOV * 0
I "Application of Electron Microscopy for Alloy Structure Studies.0
report presented at the 3rd Conference of Higher 4dreational Institutes on Strength
and Plasticity of Metals,, Petrozavodak State University# 24-29 June 1963

S11811651005100110161064
B102/B186
AUTHORS: Usikov, M. P., and Utevskiy-, L. M.
TITLE: Electron microscopic study of the polygonization in
nickel and Ni-Cr alloya
PERIODICAL: Fizika'tverdogo tela., v. 5, no. 1, 1363, 100-107
TEXT: The changes that occur in the disloc-ation structure when a
material which has been elongated 5% is heated were studied on 30-50P
foils of nickel and nichrome using electron microscopes of the types
U)MG-100 (UEMB-100) and JE1,T-6A. It was found *that owing to the polygoniza'.
tion a hexagonal and sometimes a polygonal dislocation network is formed.
.The differences in the polygonal dislocation structure of Ili and Ni-Cr
must be ascribed to the primary differences in the dislocation
distributions. They are connected with a decrease in the energy consumed
in the destruction of the packing when Ili is alloyed with Cr. Before their
elongation all the specimens were heated to 10009C in vacuo. After the
elongation they were heated again, viz. nickel to 400-900, Ni-Cr to
600-11000C, and were kept at these temperatures durifig periods of from
Card 1/2

S/181/63/005/001/016/064
Electron microscopic study of,the ... B1,02/B186
10 see to 100 hru. Conclusions: After 0.5 - I hr polygonization in
practically completed in Ni at 7000C and in Ni-Cr at 9000C. It can be
concluded that ascending character of the dislocations is rendered more
difficult in Ni-Cr. This can, however, not be attributed to a hindered
selfdiffuaion but to the large width of the split dislocations which
increases with temperature. In regions where one slip system with
dislocations with one sign are effective, polygonization takes place
according to the Mott scheme. If several slip systems are effective
simultaneously, a dislocation network is formed on polygonization: in
Ni-Cr it in a plane, mainly hexagonal network, in Ni it is a less
regular spatial network which may part*ly be plane. There are 6 Aligures.
ASSOCIATION: Institut metallovedeniya i fiziki metallov TsNI1CbM, ',,oilkva
(Institute of the Science of Uetals and Physics of Metals
of TsNIIChM1, Moscow)
SUBMITTED: July 20, 1962
V
Card 2/2

ORLOV, L.Q.; UTE;VSKIY, L.M.
Microtwins In iron deformed at low temperatures. Fiz. met. I
metalloved, 16 no.4r6l7-619 0 163. (MIRA 16:12)
1. Institut metallovedeniya I fiziki metallav TSentrallnogo
nauchno-issledovatellskogo instituta chernoy metallurgii.

USIKOV, M.?.; UTZ;VSKly, L.M.
Direct observation of the interaction of dialccations with parti-
cles of the second phase. Zav.lab. 29 no.8:944-948 163.
(miu 16:9)
1. TSontr,--ltn3-,r nauchno-issledovatel'skiy institut cherijoy m5tal-
lurgii imeni I.F.Bardim.
(A.Uoys--ble tallography)

ANTONOVA., V.A.; 77~`T, -L-M-
The strneture of steel following low-temperature thermmechimical
treatamt, Dokl. AN SM 2J+8 no*98325-327 Ja 163.
(HIRA 16t2)
1. I~stitut metallovodeniya i fiziki metallov Mmtrallnogo
nauc~mo-iWedovatellvkogo institut chernoy metallrrgiio
Pre6tavien'o akademikom G.V. Kurdyumov7m,
(Steel-Testi-ng) (Metalo at low unwratures)

ROYTBURD, A. L.; USIKOV, M. P.; UTENSM, L. M.
"On the creep nc-ch-wrii'sm, Gff ni-kell and its aLlcy-s."
report submitted for 3rd European Regional Conf, Electron Microscopy,
26 Aug-3 Sep 64, Prague.

SPASSKTY, M. N.; UTEVSKI"f, L. M.;.KJiA-SIMDV, F. R.
"On the P(~.culiaritie3 of ,~r;artenz'Lt,~ forming In rieform-11
report submitted for 3rd. European Regional Conf, Electron Microscopy, Prague,
26 Aug-3 Sep 64.

ROYTBURD, A.L.; RUTBERG, V.P.; USIKOV, M.P.; UTEV L.M.
Microstresses in polycrystals. Fiz. tver. tela 6 no.1:32r,,322
ja 64. (MIRA 17t2)
1. Institut meta).lofiziki, Moskva.

I --r- I - I ~
by Finskor O~asis -of diffractional
methods of investigatf6h of parf&-Ct crystals"), B.. 11,
Rovinplc~.y and L. 11. Hyba% ostigation of 6-6b6ndenoo
_9va ("Inv
proportios on characteristics of structuro
of metals"-). L. Mo 11tovskiX and P. X.. Usilcov ("Applioation
of microscopy in investigation of structure of alloys"),
A. A. Pradvoditelev and N, A Tya.ngnina ("Role of repro-
iiT"~_r~_o'cess of plastic flow"), A. Ve..
,ertsov V. Pertsov and E, D. Shukin 113elf-producib~z
ntern-al disloaraion of metals under action of strongly
superficially-active,-metallie melting"-) and 1, L, Mirkin
'("Probl-ems' of structural investigations adv_&_no-e-TWj-~~
requirements of progress of tachnology"5. ___ -
I I
it
rer,orts presented at the 3rd Intervuz Conferonce an Strength and Ductility of
Metals., Petrozavodsk State University, 24-29 June 1963.
(reported in Fizika 1-11'etallov i Metallovedeniye, Vol. 16, No. 4, 1963, p 64o.
JPRS 24,65;1 i9 may 1964.

F
S- D (M) --3 rue r, RJD/Ifd ad
rjp(,,
,. AM. ~ISDASD (f -Z/
ACCUSION NR; AP,1049464 //6 4/1 S9/002/(- 3 17/0 3-2- 0
AUTHVRS: 2pytburd, A. L.Y ILts-1kaxL -ft. I!,; Utevskir,
TITLM On tM mechanism of plastic deformation in stationary creQ2
of Metals
SOURCEf. AN SSSR. Tloklady*,' v. 15~* no. 2. 1964-1 317-320, and insert
318
TCpIC TAGSr plastic deformation, creep, dislocatfon study, tTfirb-
cation motion, nickel alloy
-ABSTRAbTC-~----A-.--eLectr- -o--n--Ihidtdsc(!93-cl.studv--was--made- of -the -dis'iocatiow.
structure Produ-ced -'durlng the creeo- procesa. 'Phe purpose of 'the
study was to chick wbet-.',er diqloca-tlon mction can
a -- t ,., ~a I I ,, b e ;iril low
j j6 e MITI
Curd
1/3-

L 176-88-65
ACCESS1014 Nf~: AP4049484
thick) were deformed under cr-~~ep conditions at 700C in vacuum. To
fix the dis'.ocation structure, the samples were unioadec: oi,,!,,, after
total coolina. The %lamples were then electrolytically 1),:)Iished an6
cbserved in a JEM-6~"Itelectron microscope"rjat 80 and 100 I:V accelerau-
inq voltage. The main elemerts cObserved after creep are heli.coidal
dislocation whose shape is di,;torted by the., plastic dejEormation.
This.- dislocation has an appreciable velocity of._non-,zorxs,a_rvatjz_ve
motion,- g-I.V,2.nc; -rise to- a plastic deformation rate of 10-5-10-6
67l.;---It-is concluded that--in.--contrast to earlier opinions, a con-
siderable f raction-co-YE the-dellarmatIoni if--not -all, - in high-tempera- -1.
ture static~nary creep is the result of noncoi,servative motion of
hellc3idal dislocations, lip ted by closed self-diffusion flow. The
origin of t.he s1ocati(,-)nq cills for addi-r-Lcrial study. This report
was presented by V. Kurdyimov. Orig. aft. nas: 3 'L;-t~res a-nd
4 formulas.
ASSOCIATION: Institut inetallovedeniya i fiziki rinietallvv Tsentral'-

CID Zrl
L Ax TOO
.-AcclESSION UR.* -AP4049484'-
no;o nauchno-i.3sledovatel'skoqo instituta chernoy metallurgii 'in-
stitute of Mletal Research and Metal Physjilcs- Central Sc-~en-
tific Research Institute o' Ferrous Metallurq~,)
SUB14ITTED: 07May64 ENCL: 00
SUB, CODE: 101, SS 11h REF SOV; 004 OT HER: 002
Card 3/3

Ffflp(vi lip( C 11 PX/ jD
IT, 17. P.T':~ V.L.:~~ V.1
Utevski 4
=M
T ITIE Elaotron microsro tho dislocatloa- x
;stru.et,ure of nie~kella its alloys
SCURCE: Dne.)ropotrovsk. Ins,"Itiit motaII,)v,)daniya i fizlki mate.
Problem-y rmat a1lovedaniyct i lfizlkl. metallov, no. ~), 1964, 77-1~O
I.. metal -te&,aninal prcoertv,
allay.-
ABSTRACT: "ho nickel: --a-11dre i-twastigated were W_ VINL 3% chromium),
UL 9. 85COI
zo ribbo
,in
Card :VI;!

foil ~imv ~ILT5011265:
mechanical tfssta, The ribbon -war, cut into samples 150 ran long which
were anneEdo,i a" 1,0000C (aIr PIPczt-Ir- deformatIon of fha
sami.ie:3 wai n x t s n n

a nd deformt Lon wita tima waS v C.,
vq e .3 rn I no c,

str%ctu-e fo-mad by coI-
r e,~ ,~ f I o f r ma r I a ;-r t t3 7 t"- ~q, a -i
n ~tr - P 1 lo-, s ~,e r~ oma s ~c 1 -_ '*'a-,, , it r
under the S~me deformat:10,11.z.
of the two-ptir-se alloy a-re pro a e n r; e 7.

._3t.rj*_-;u-,,ion of dI'IqIoca-.iE:;r,.L,- d4urlnj-
Th3 -Orli
L 7 3 x ne r !:nr- _n :-1-r ",,,ova m~;_-u% e
n
e a !,L, - nc,,-. a 1 .3 E) Cr ~T, ~,A

ihie;h temparaturo d0formatdWI*

- ---- --- -------
L 51-198 6,5
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str-lo tw, a ir the 0 y
A S S
in.; t i I.u t .3
3 TLT DL I- '7!=-
jlfR REP SOV: 010
OTIM: o

UTZVBKIYI L.No.; -
Suropm Conference on Mactron Kicroscopy. Zav.lab. 30 no.32&1521,,.2525
064, (KIRA IS 11)
I

L 5-z;,-D C- t f'~ 7 1~ E!I,
L ff fr-,~ n -'Yl !IrAe,
frl= h'Ate-
TOPTIC T", LOS or,.SGI, wohdl--'147~ daPrr-ito oteoA. clectron miarcml~cp*, rrxbiecz,
100 '!k?, g! 69c~R EtMel. rteel, IMI-15'.ZaZ~ e-Oelj

were Ubiibitod. --mo rf-~-a-'Itr r-~.cv in-homa-Ceneous e ax saturation in tht
zonas" " '.Fl th's -'riciaty C-f tile imid & wiph la-,,er acygen ctm~ont was ubaervod
than in tho rAWI. pro,,%er. The carbide test. ahomd Lhat turva~on Was pre.!I~,-.nt,
exclusivel,- a oolid Ec~lution. The Ole ctmn-ixxicroemc-,~p jod the
1~1 I-P
~,-nutf of I"q !01-t
fol ~.eLL al
q-- 'Laf" , 13 6
C".)-,erved 1-t.e fornm of p-6r.43 ~k,~ 2.C r. 1 -al a-',*:3 C.
t,,i H-9, ~ r ',7-je c&rtJ-A-- t.:-"3 noc 0 5 5D 9
boun a r ~' o L --I a I'
A33, r I OR -761MGM
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Sj akf.STO I W &4L z 00 SUB cmz;t
uo W Sov c 002
co;d

SPASSKI[Yv M.N.~ IIT'EVSKIY, L,M.,~ KWILIMOV, F.P.
stru-.cura &M It.3 ,taing6e a3 a rnsult, cf therzc~--
treatment.. Piz. r-,,3t. 1, metal!,-wed. 20 L,~-4~614--
62~-- 0 165. (MIRA l8slij
". Uentrallnyy instittit. nlie:-noy
installurg-i!t lm&nt I.P.BarlIna.

L -27450-66' E:V(T(m)AWA(d)/T/EWP(t)/EWP(k)AWP(z ~/~Wp
UR/O I
ACC Nito AP5027150
AUTHOR: Spaaskly, .11.-; Utevskiy, L.M.; lalashimov F_ R.
ORG; Oentral Research Institute for Perrous Metallurgy im.
(Tsent-re-19i,ij nauchnolooledovatel'okly Institut ohernoy met
I.P. Bardin
TITLE: Struature of martensite and Its changes as a result of heat and
mechanical vorking
SOUROE: Fiz:Lka metallov I metallovedeniye, v.20, no.4, 1965, 614-621
TOPIO TAGS: martOnsite steel, austenite steel, work hardening, metal
heat treatmeat
ABSTI'MOT; vie article presents the results of au electron microscope
Investigatiou of the fine structure of martensite and the dimensions and
the dis rie tation of Its blocks a fragments. It.compares the results
of*t;e;to. a t'r conventional harden and after heAt and mechanlcal
treatzaent.r~ktmples of alloy N30F24gnd steel 40n27 wero prepared by cold
rolling ;0t% form of strips approximately O.I'mim thick. Heat and
mechanical treatm nt of the previously annealed strip was supplemented
0
by rolling at 5 0. After this treatment, the samples of alloy N3OP2
and steel 40*1427rTere almost completely austenitic. The twinning of
martensite FrE.-ys-Vals, obseried in iron-nickel alloys, is found also in
UDC:

L 27400-66
ACC NRs AP5027150
other alloys, including steels with a martensite point below 2000. A
twinned structure is also characteristic of 4ON27 steel. The relatively
low density of defects in martensite alloy X3OF2 makes it possible to
observe the erfect of the austenite deformation on the structure of the
martensite forming within it. The experimental results show that a
40% deformation of the austenite before the transition leads to
creation of a. very high density of defects In the martensite. The
authors conclude that the heat and mechanical treatment of steel leads
to supplementary breaking up of the martensite crys-ale into fragments
whose size corresponds to the size of the cello of 4he dislocation
structure of the deformed auotenite. The reciprocal disorien ation
of the fragments reaches 10-15%. Orig. art. has: 8 figures.
SUB CODE: HM/ SUBH DATE: 22jul64/ ORIG REP: 005
ON REY: 003

T T 11 of F(Ci
--- A-3 3-2 L
ACC NR:
R/oo58/65/OU0/'()!1/
SOURCE CODE: U
the. i luence of alloying of Ni on the character of its dislocation structure pro-
duce ing the course of hardening under different conditions of plastic deformna-
, ZEU
tion, bgrmal loss of hardness, and under creep conditions. Alloying with Til;j~_r!'v
and AlVeads to a decrease in the enerM-r of the stacking faults (7), which 1S_
in the appearance of flat clusters rf dislocations in the single-phase alloys (at
small degrees of deformation). It is shown that during the earlier stage of aging
(alloy of the "nimonik" type) the dislocations cut through particles of the secord I
phase, whereas the larger particles which are produced during the later aging stage
are circuited by the dislocations. Upon polygonization one observes,the formation ofl
more or less regular hexagonal grids of dislocati=s. In creep, Matic loops of
Card 1/2 1
AU'lliOR: U-il'oi' P. "'tt:v~;kdy, L.
TITM: fnvestigation of the dislocation' structure of nickel and
4466 allov,-,
V
SOURCE: Rcf. ~~h. Fizika, Abs. 1u,,349
REF SCAJECE: 1i':). tr. In-t metalloved. i fiz. metallov Tsentr. n.-i. kij-JR
metallurgii, rfp.
TOPIC TAGS: nickel, nickel allcry, cryatal dislocatiorypsamwwArmr, metal hardenidg,
crystal defect, plastic deformation, creep/
ABSTRAC : By direct transmission the authors investigated in an electron microscope
C

L 33248-66
ACC NR, AA/JI()2__'()
dislocations and helicoidal dicl~;cation3 are produced. Possible causes of the harden-
ing by alloying (Incluajrq), a two-ha.,;c itllqi), the mechanism of polygonization, and
creep are discutmed In IAVht wl the resxilti3. M. Usikov. (Translation of abstractj
60 CODE- 20
Card 2/2

,~6 ~_CW VjAj/E'dP(w)ZT/i;WP(t)/j~,T1
_11D
kj?
ACC NRI AP6012230 SOURCE CODE: UR/0129/66/000/004/0001#/0006
AUTHOR: U tevski y, L. M., Kashimov, F. R.
MIG: TsNllChMIE'T
TITLE: Dislocation structure of hot-worked austenite and Its "inheritance" by
martensite
SOURCE: Metallovedeniye I termicheakaya obrabotka metallov, no 4, 1966, pp 4-6
TOPIC TAGS: austenitic steel, crystal dislocation, hot working, austenite,
martensitic transformation/N3OF2 austenitic steel, 40N27 austenitic steel
ABSTRACT: The question of whether defec,~of austenite are inherited by martensite
entally investigated with the d of electron diffraction microscopy.
was exper9d(
307
SpecimensW the austenitic steels N30F2 Fe, Mi--2% V; T _500C)
itart,trans,
and 4014271(27% Fe, Ni--0.4% C* T r 700C) were ei er mmedi tely water-
t'
quen-ch-ea-from 1100*C or hot- rOe ffel*_- v - 50 cm/sec, t - 6-507.) at various
io
temperatures prior to quenching. _4e necessary amount of martensite was obtained
by cooling the specimens at temperatures -20*C below T~art.trans. Electronmicro-
scopic examination showed that for specimens of both steels the dislocation density
1/2

L
ACC NR: AP6012230
increased with degree of deformation; high-temperature deformation (hot-rolling at
550-1000*C) of auatenite, even when performed at a fast r te and immediately
Ia
s f
followed by acute cooling, is accompanied by a process f the polygonization type,
dkr er
a
however, and the total dislocation density markedly d reases; if, on the other
he
hand, it is riot immediately followed by acute coolin he stability of dislocation
:
formations increases, the subgrain boundaries get finer and more ordered, and
ultimately this entire structure is eliminated by recrystallization. As for the
austenite-martensite specimens, it was found that martensitic crystals indeed
inherit the dislocation structure of austenite: the dislocation boundaries of
austenite do not terminate at the austenite-martensite interfaces but continue in
martensite. This is not a general rule, however, since, e.g. certain most mobile
dislocations may be "swept out" by the growing cr,,jtal of martensite. Therefore,
.the term "inheritance" must be applied with rev,.rvations. Thus, low-temperature
deformation (