SCIENTIFIC ABSTRACT LEVITIN, S.M. - LEVITIN, YE.A.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000929620015-7
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: July 12, 2001
• Sequence Number: 15
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

On the Problem of the Influence of the Electric SOV/'/7-58-6-17/37
Field in a Cathode on Its Electron Emission
the field (and of the current) is not essential in this
process. A corresponding generalization of the reoults from
reference 2 is also carried out with respect to the pas:,a.,c
of current through electron tubes. Tile problem of the
emission of a gas not in equiLibrium can be ge.icralized as
follows: If a current I passes through a semicondutor or
a metallic cathode two phenomena necessarily occur in tile
cathode: The heat effect (determined by I R) and tile effect
of the electric field (determined by IR). These effects may
occur in three principal quantitative ratios: 1) The heat
effect considerably exceeds the "field" effect, 2) Both
effects are about equal, 3) The " field" effect consider--bly
predominates above the heat effect. If the cathode is driven
by pulses the conditions for a relative increase of the field
effect are more favorable. There are 3"refere ces, 3 of
which are Soviet.
Card 2/2

VLASOV, Vladimir Pedorovich [deceased]. Prinimali uchastiye: RATUSKET, V.A.;
LXTITIN, S.M.; GALTA4, A.De; AYANASIMCTA. A.P.; HIKITIN, N.A.,
6t ".4d'; HISHCHU11" V.I..,ted.; KARKOCH, K.G., tekhn.red,
[Electronic and ionic d ices] Blektronnye i ionnye pribory.
Isd.3., perer. i dop. skva, Goo.izd-vo lit-ry po voprosam eviazi
1, radio, 1960. 733 p. WRA 14a)
(Blectronic apparatus and appliances) (Ions)

XAXSIMDV, Tu.M.. kandidat takhAlcheoklkh zauk; IZVITIN, S.S.
Generalizing operation practices of open-hearth furnaces vith magnealto
chrome crowns. Hatallurg.ne.7:19-21 --Jl 156. (K6U 9:9)
l.Starshiy swichayy setrudmik TSeltral '11*9* nanchao-issledevatellsksgo
instituts, cherney matallurgli (for MAksimov).2.Rukeyeditell ppjr Gosu-
daretvannege soyuzzoge instituts. "SUllproyaktu (for Lovit,
inr
(Open hearth fw-aaces) (Yirebrick)

- I
I-W4TS---V , ;.'rcr.A n IMI I'. I iay 1 -, v -1 -, h :N---.4KO , VVJKha 11 A v I, sent lye. vich;
. , Geraiadly Akiz-vich, -Soj,-mon
,)I-
, , Jwn-avich
S
[Open-hearth Purna--,os; an atlad Martenovskie pechi; atlas.
Mosimp Xota2 jurivilar 11465. 177 P. (YLqA 18:8)

LEVITIN V.
---
Introduction of business accounting on Kam Steamship Line Yeanels.
Rech.transp. 20 no.6:12 Je 161a (MIRA 14:6)
1. NacWln:Lk firm ovogo otdola Kammkogo parokhodstvao
(K&= rdyer-Inland vater transportation-Accounting)

SOV/ 137-57-6-9845
Translation from: Referativnyy zhurnal, Metallurgiya, 1957, Nr 6, p 75 (USSR)
AUTHORS: Eydis, S., Levitin, V.
TITLE: The State of the Art of the Collection, Processing, and Utilization
of Nonferrous Scrap and Wastes (Sovremennoye sostoyaniye sbora,
pererabotki i ispol'zovaniya loma i otkhodov tsvetnykh metallov)
PERIODICAL: V ab.: Rate. ispollzovaniye struzhki i dr. otkhodov chernykh i
tavet. metallov. Moscow, Mashgiz, 1956, pp 378-386
ABSTRACT: Secondary metals occupy a significant position in the total con-
sumption of nonferrous metals. Thus, secondary Cu, Al, and Zn
constitute >113 of the total of these metals used in this country. It
is therefore necessary to adhere strictly to the rules for collection
and storage established by a special standard according to which
scrap of each metal or alloy must be kept separately. With this
purpose, all machine tools are provided with trays and other equip-
ment for scrap collection. There.'jis a complex of measures with
the objective of assuring and stimulating careful collectionjAnd
proper storage, as well as delivery of nonferrous scrap anii rejects.
Card 1/2 Thus, 10% of the monies derived from scrap sale is expended by the

SOV/ 137-57-6-9845
The State of the Art of the Collection, Processing, and Utilization (cont.)
various establishments to carry out measures to improve collection and storage.
Higher prices are paid for scrap delivered in unmixed form and with a rating
sheet than for mixed and contaminated scrap. Thus, the price for clean Cu
swarf is 89% higher than for dirty, unrated swarf. The corresponding price dif-
ferential for brass swarf is 447o, for Sn-bronze 3676, and for Al swarf 6176. Care-
ful preparation of the chip is needed before remelting.
G.S.
Card 2/Z

DUBROV, N.1 LEVITIN# V.
Results of creative cooperation. NTO 4 no.9s17.18 8 062.
(KEPA 16ol)
1. Predsedatell soveta Nauchno-tekhnichaskogo abahchestva
Urallskogo nauchno-iseledovatellakogo institute, chemykh
metallav (for Dubroy). 2. Mhanyy seicistarl soveta Nauchne-
takhnicheskogo obabehestya Ural'skogo nauchno-looledovatellskogo
institut-a chernykh metanoy (for laiitin).
(Research., Industrial) (Technological innovations)

L 2678-66 EWT(d)/EPF(n)_2/EV.'P(l) IJP(c) 0/13C
ACCESSION NR: AP5021855 UR/0280/65/000/004/0119/0125
AUTHOR; Levitin, V. F. (Moscow); Skripkin, V. A. (Moscow) _B
- ~ 4ti 0
TITLE: The synthesis of correcting devices of linear systems for a given
accuracy at a fixed instant of time
SOURCE: AN SSSR. Izvestiya. Tekbnicheskaya kibernetika, no. 4. 1965, 119-125
TOPIC TAGS: linear automatic control s stem, linear system, linear control system,
control system stability
ABSTRACT: In the majority of cases the structure of the system under design and
the distribution of its known loops as well as of the correcting onea (the para-
meters of which have to be determined) are given in advance. The authors show that
for systems the accuracy of which is essential only at fixed instants of time,
stationary circuits may be used as correcting loops securing the agreement of the
characteristics of the projected uystem with their optimum values. The notion of
equivalent systems having equal accuracies at a fixed instant of time is introduced
and the properties of such equivalent systems are studied. Formulas for the
determination of the transfer functions of stationary correcting loops are also
derived. Orig, arte has: 33 formulas and 3 figures.
1_CQrd. 1/2

L 2673-66
ACCESSION NR: AP5021855
ASSOCIATION: None
SUBMITTED. 24Har64 ENCL: 00
No REF SOV: 002 OTHER: 002
Card- 2/2-
SUB CODE: DP, IE

Card 1/1 Pub- 17-22/23
Author :Gorkin, V. Z. and Levitin, V. F.
Title :Modification of a photoelectric apparatus for the investigation
of "electroforegramms" [electrophoresis diagrams] (on the method
of quantitative microelectrophoresis of proteins on paper)
Periodical :Byul. eksp. biol. i med- 7, 76-79, Jul 1955
Abstract :Authors describe an apparatus for quantitative microelectrc-
phoreais of proteins. This instrument is a simplification of
Hoettger's apparatus (Klinische Wochenschrift Vol 3, P 85, 1953)
and is built entirely of parts produced by the radio industry of
the USSR. 14 references, 4 USSR, 15 since 1940. Diagrams,
Graph, Table.
Institution :Biochemical Laboratory (Head: Dr. Biological Sciences B. S.
Kasavina), Central Institute of Traumtology and Orthopedics,
(Dir: corresponding Member Academy Medical Sciences Prof. N. N.
Priorov) Ministry of Health USSR, Moscow.
Stibmitted : 18 Nov 1954

M
LEVITIN9 V.F. (Moskva); SKRIPKIK, V.A. (Moskva)
Synthesis of the correcting devices of linear system with
given accuracy in a fixed moment of time. Izv. AN SSSR. Tekh.
k1b. no.W19-125 Jl-Ag t65. (MIRA 18:11)

- -1 . A . 7VITIN x .- . 7- V. a. ___ __
1S2UNvI4s-j'- , V.-Ira.; _ItUUNf!MYIi,_,
"Secondary Nonferroua MietalB (Handbook. Part I- J.',reparation and Preliminary
,Working).n Metauurgizdat., 1950. 475 PP-
C nts and evaluation B-77881, 16 Aug 54

ISTRIN Mikhail Alaksandrovich- IXYITIV Tuitf D&nanovich- RUDINSHIM,
losif Grigorlyevich; MIW-R-."FU~ou WIIM~Iovlch; XILIJR, L.Te..
k&ndldat takhnichasir"ch nauk, r*ts*nzent; BIWT. T.Ta., redaktor;
CHXAkOT. A.B.. radaktor; ARKRANGILISKATA, M.S.. redsktor isdatell-
stval MIKKAYLOTA, T.T., takhdobaskly redaktor
(SecovAary nonferrous metals] Vtorichw* taystare metally; spravoch-
nike Isde 3-s. parer* I dop. P*4 red* T-U-Belova. Kookys,. 0o&.
nau4hno-takhn, Lid-vo lit-ry po chernot i tsystnot metallurgil.
Pt.19 [Procurement and prixwT processing] Z&Sotovka I pervichnala
obrabotka. 1956. 558 p. (KIRA 9:7)
(Nonferrous metals)

ISVITIN, V.P. ~- -,
--,. --- - On year round sconosdo accountability for river vessels. Rech.
trans. 18 no.8:24 Ag 139. (MIRA 12:12)
l.Fachallulk finansovoto otdola Kamkogo parokhodstva.
- (Inland water transportation,.--Accounting)

Acassiox NRt Amol4W
8/0137/63/000/012/VO48/VO48
SOURCEi RZhe Matallurgiyat Abse 12V353
AUTHORi Kagans As Sol-Levitinp V. S.; Ostrovskayap Ye
TITLEs Some properties of vacuum steel used in the production of instrument
bearings
CITEED SOURCM Tre Vass* no-Le konstrukto-takhnole In-ta podshipnike prom-stip
no. 1 (33)8 1963t 49-53
TOPIC TAOSs Instrument bearing steelp vacuum steelp vacuum steel remelting,
steelmaking
TRAMATIONs ShW5P steel- for U-A pwduction of precision instruxent bearings
is made by the following methods 1 1. Double vacuum remelting of consumable
electrodes made from high-purity charge materials (carbonyl Fop spectroscopically
pure Cp crystalline Sip etoo)e 2~ 'Single vacuum remelting of consumable elec-
trodes which were first subjected to alectroslag remelting* The billets for
Card 2/2

Acassm NR, AR4ol4U2
electroslag remelting an melted by the usual process in electric are furnaces,
3. Single vacuum remelting of consumable electrodes melted by the usual process
in electric are furnaces. Investigations of the quality of the metal melted by
these methods showed that the metal melted by the first method in the purest with
respect to nonmetallic inclusionso Steel made by the second method is contaminat-
ed with point nitride inclusions, for the elimination of which a double vacuum
remelting of the elaotroslag metal is proposed* Go Lyubimovao
Dsm AcQ, o9jan64 SUB ODDE: ML ENCLi 00
Card 2/2
IT,

1w,11TIN, V. V.
MSSRIPhyaIcs TochnIcal I hysics
Card 1/1
Authors Palatniko L. S., and Levitin, V. V.
Title i X-ray investigation of alloya Sn-3ej Zn-gep Od-Se and Ag,-Se
Periodical Dokl. AU SSM, 96, FA. 5j 975 - 978, June 1954
Abstract In the present article, the authors present the results of the., chemiCAI
and themal invebtiritions of the binary ryntemn of alloy3, an llatnd In
the heading of this article. The preparation of the typei of samplen
used in testing by meani of X-rays is de~llt with, and the arfect. of
the various heit treatm,~nt3 on the proT-rties of thp- in,lividual allnys,
relative to their stability afhq:, and trtkn-,j7.--U'V?1C.'~ of (if the
vItreous films, is drserlbed. Rve 1-ul-I 1 f3herl in
(1936-19412), and one Cerman roiference of 1931. On,-! table.
Institution The A. M. Gor~iy Ittatm Univer.,iit.,.- of KK-irkov
Prenenf.t-d by: Academician, !). A. VekrUn!;Viy, Arxil 10, 19,11,

!-B(3)9 18(7)1 24(2) ~301/126-?-2-32/39
AUTHORS: Levitin, V. V. and Syreyslichikova, V. I.
TITLE: ' The Influence of Boron on the liatu--e of Carbide
Separation in Austenitic Steels During Tempering
(0 vliyanii bora na kharakter videienlya karbidov
v austenitnoy stali pri otpuske)
PERIODICAL: Fizika Metallov i MetalloveAeniye, 1959, Vol 7, Nr 2,
pp 308-310 (USSR)
ABSTRACT: Heating of austenitic stainless rteels containigg carbon
in solid solution up to temperatures of 500-800 C
causes formation of chromium carbide in the grain
boundaries, as a result of vAic.h the steel ceases to he
resistant to intercrystalline corrosion. The authors
investigated the influence of small additions of boron
on the nature of the separation of the ca.CL.de phase
u
4
during tempering and on the ten,31eacyo
manganese nickel steel contai!'.11-'.~' ;4 Vo intercrvs--.~!lline
corrosion. The above steel has -Ienn studit3l in tlv~-
work of Levitin et. al. (Ref ir Jots ~'C- W~Iic-
various quantities of boron hav., -x,,c:-n t' dded were
in a high frequency furnac,3 and, f-;r:-,'f.,d into rods. 'I'M
Card 1/5 specimens for metallographic i-riveoti,.ation and fo.-

30'7/126-7-2-712/39
The Influence of Boron on the Vature of Carbide Separation
in Austenitic Steels During Tempering
inte rcrys tal line testirjl,;- made from the rods w8re heated
to various temperatures in the range 950-1250 C, hold
for one hour and quenched in water. Tempering was
carried out gnder the usual conditions (Ref 3~1 for tv~o
hours at 650 C. The tendency to intercrystalline
corrosion of cylindrical specimens of 3.4 mm diameter
was determined after boiling 7,hein in a standard
solution (Ref 3) by the lost; of' -aetallic sound gn f0114 n~
and by the increase in electri:; resistance. The
investigation has shovai thalv- bcron slo-.ris dovin IV-lie
formation of the carbide lon, th(.- aurtonitic
grain boundaries. In steelo co,.11-aiain- no boron,
temperin,'- for 2 hours at 6ciO"". -au.-~cs Afor-matiun, of a
continuous chain of carbidi,,s '-LjjnL the grain boundaries
(Fig la). In steel containint; 0.004% boron, the carbide
phase separates ia the form of fragments; the 6rain
boundaries remain pure alon6 considerable lengths
(Fig 1b). At concentrations lower than 0.003% or above
0.010% boron has no influence on the formation of the
carbide network. A retardation of the decomDosition of
Card 2/5 the solid solution in the boundaries under "Qh'e influciice

'O'OV/126-7-2-32/39
The Influence of Boron on the Nature of Carbide Separation
in Austenitic Steels During Tempering
of boron is observed when heating for quenchinf, is carried
out to temperatures of 1075-1150 C. At lower or higher
quenchin g temperatures, the carbide network formation
occurs in the same way as in steel without boron
addition. The influence of boron is the greater the
lower the carbon content of the steel: In 0.06% C steel
boron practically completely prevents formation of
carbides that can be seen under th4e optical microscope;
at a carbon content of 0.14%, t'112 influence of boron
becomes negligible. From the TaUle i-:; can be seen -that
steels containing optimum boron ~.4)ntents recist inter-
crystalline corrosion tests acc-)rdin~: to GOS"." E:032-51.
The results of the investigation obtain,~d
V. I. Arkharov's theory of prefe~:,~atial diE;t--;bUt-1On of
impurities in the grain boundaries as result of the
tendency of the alloy to lower 1-ts exces-- surface enarg
(Ref 4 and others). AccordinL, ~.v V. I. Aricharov (Ref U,
the mechanism of the influence of boron or, the ability
of structural steels to be temnered consists in the
Card 3/5 fact that the enrichment of intercrystalline boundaries

MV/126-7-2-3P/39
The Influence of Boron on the hature of Carbide Separation
in Austenitic Steels During Tempering
with boron leads to a decreu--;e in the distortion of the
crystal lattice as a result of which the work for the
formation of critical nucleation of the separatinC
phase increases. This explonation is applicable
apparently also to the effect shown in this viork.
The decrease in diffusion rate in the grain boundary
zone (Ref 6), in this case of carbon under the influence
of boron, -md the ejection of carbon fron the boundary
zones can also be factors influeneinC the retardation of
carbide particle formation. Lot us note that boron
retards the separation of exce-1-- -phases f:,o;2 austeni"U.-
of different composition (carbon and alloy steels ?
austenitic stcel). The surface activit-,- of boron is apparent
in nickel base alloys (Ref 7) and in icon (Ref 6). JUnoing
the number of factors influencinG intercrystalline
adsorption (Ref 9), in the case of boron the determining
factor is a geometrical one. The atomic radius of boron
is smaller than the radius of atoms forming a
Card 4/5 substitional solid solution in the alloys listed, but is

LOV/126-7-2-32/39
The Influence of Boron on the Nature of Carbide Separation
in Austenitic Steels During Tempering
greater than the radius of atoms going into solution
interstitially. This is hound to lead to a Ereater
solubility of boron in distorted orain boundary zones
as compared with the solubility ir. the grain bodies.
It appears that in the construction of intercrystalline
boundaries boron atoms play a smaller role as "structure
material" than metallic atoms.
There are 1 figure 1 table and 9 referencesl 8 of which
are Soviet, 1 English.
(Note: This is a complete turanslatian except for the
fl-gure caption and table)
ASSOCIATION: Urallskiy nauchno-issledovauellskiy institut
chernykh metallov (Ural Scientif:'i-c Research Insti~~-Aite
of Ferrous Metals)
SUBMITTED: May 12, 1958
Card 5/5

SOV/129-59-1-7/17
.AUTHORS: Mironov, L.V., Engineer, Sazonov, V.G., Candidate of
Techni~al 8::iences, Levitin, V.V., Engineer and
Rodigin, N.M., Candld-ai~~ ~Teij_mathematical Sciences
TITIZ: Influence of Electri~; Heating on the Properties of Cold-
rolled Stainless Steels (Vliyaniye elektronagreva na
svoystva kholodnokatanvkh nerzhaveyushchikh staley)
PERIODICAL: Metallovedeniye i Termicheskays. Obrabotka Metallov,
1959, Nr 1, pp 26 - 30 (USSR)
ABSTRACT: The influence was studied of electric annealing of the
cold-rolled steels lKhl8N9, lKhl8N9T and Khl3N4G9
on their mechanical properties, the recrystallisation
prooesses and the resistance of these steels against
interorystallite corrosion. The composition3 and the
z%in data of these steels are entered in Table 1, p 26.
The specimens were heated with spoeds of 100, 300, 600
and 1 000 C/sec --,p to 900-1 400 "'C and immediately
after that were c_-~-,led in air. From thus-treated strips
(210- --- 2200 mm), specimens fcr mechanical tests were
prepared. The results of tensile tests are graphed in
Figure 'I, p 2? and it can be seen that the desired
meohanical properties can bB ensured by electric heating
Cardl/3 with speeds of 100 to 1 000 Vass without subsequent

SOV/129-59-l-'//l?
Influence of Blectri,: Heating on the Properties of Cold-rolled
Stainless Steels
holding at the particular temperature. The optimum 0
properties are obtained after heating to 1 150 - 1 200 C.
In Figure 2, p 28, microphotos are reproduced of the
structure of -Me steel !Khl8N9T after annealing with
electric heating as well as with ordinary heating. On
the basis of the results 6f irr;estigations of the resistance
of materlair, ~;o fntercrystalli-re corrcaion, the authors
-onzlude that the prccess of recrystallization of cold-
rolled austen!.-Vic stainless steels,under conditions
pertaining to electric heatinggproceedB with a very high
epeed b-,~'V at a higher temperature zhan. in the case of
ordinary heat-,ng: acftening and the desired mechanical
prc:per'4ieB of +Vhe s-,eelc, _`Khi,8Nq.
.0lKh18NqT and Khl3N4G9
at heating 5peeds Gof 100 - 1 000 C/sec are attained
at 1 1150 -- 1 200 C. On the basis of corrosion studies,
it is concluded that the necessary resistance against
intercryetallits corrosion can be ensured with any of the
Investigated heating speeds for steels lKhl8Nq gnnd-
Card2/3 Khl3N4rj9 and with heating speeds of 100 and 300 C/see in

SOV/129-59-1-7/17
Influence of Electric Heating on the Properties of Cold-rolled
Stainless Steels
in the case of the uteel lKhl8N9T; if higher heating
apeeda are used the carbon in this steel has to be
combined first Into titanium carbide.
There are 4 figures, 2 tables and 6 Soviet references.
ASSOCIATIONS: Urallskiy inatitut chernykh metallov (Ural Institute
of Ferrous 11atala) and
Institut fiziki metallov UFAN (Institute of Physics
of Metals of the Ural Branch of the Ac.Sc.)
Card 3/3
V__ VQMIQ

S/137/60/WOA 11/04 1/t43
A006/AO01
Translation froml Referativnyy zhurnal, Metallurglya, 1960, No.11, P-265, # 27364
AUTHORSi Ltutin.-KOY.. Outerman, S.G.
TITIZ: Mechanical Properties of Cold-Rolled Stainless Chrome-Manganese-
Nickel Steel Containing Nitrogen
PERIODICALt Byul. nauchno-tekhn. inform. Urallskiy, n.-i. in-t chern. metallov,
1959, No. 6, pp. 77 - 79
TECT: The authors studied the effect of the degree of cold deformation
(15 - 40%) on mechanical properties ( 6b,& ) and corrosion resistance of two heats
or cold rolled Cr-Mn-Ni steel containing In %: C 0.13; Cr 17.7 - 18.0; mn 6.7
7.9; Ni 3.5 - 4.8j S1 0.3 - o.4; N 0.12 - 0.24. It was established that the
steel Investigated showed a better combination of strength and ductility than
IX 181-ig (1KhMq) steel and that It was able to withstand IntercrystallIne cor-
rosion tests by the method given In A-1 GOST 6032-51. There are 2 references.
T.F.
Translator's notet This Is the full translation of the original Russian abstract.
Card 1/1

874142
S/123/'6Oj"0/t24/002/'C I
A005/A0Ol
Translation from; Referativnyy zhurnal, Mashinostroyenlye, 1960, No. 24, P. 16,
# 132065
AUTHORS: Meandrov, L.V., Golldshteyn, M.I., Levitin V V
TITLE: The Determination of Deformation Resistance of Alloyed Steele at Hle.
Temperatures
PERITODICALl Byul. nauchno-tekhn. inform. Ural'skly n.-I. in-t chern . metallov,
1959, No- 7, pp. 59-66
TEXT: Results are presented from the determination of deformation resistanc.
of steels 4oAq (4oKhN), 4oAH2M (4oKhN2m), and 40 X-2H2M ~40MMM) under st-atic
tension and dynamic compression. The diameter of the tension samples was 8 Mm,
the gauge length was 60 mm, the tension speed was 1.0-1.5 mmlmin, the test *-em-
peratures were 900, 1,000, 1,150 and 1.2000C. The compregalon tests were condu,~'.
ed on the frictional pressing machine. The cylIndric samples were 20 mm in dia.
meter and 14 mm in height. The dmwnstroke speed of the pre-zz slider with the
I
striker was 180 mm/sec which corresponds to the Jeformation rate of 7-8 sec-
Card 1/2

87442
S11 23/60/000/024/*002P 14
A005/AOOl
The Determination of Deformation Resistance of Alloyed Steels at High Temperaturei
All steels showed at small deformation degrees the strain-hardenLng being +he
greater the higher alloyed the steel and the lower the temperature. The highest
strain-hardening was observed with steel 40MMM, the lowest wv-h steel 4OMv4,
which is obviously connected with the decrease of re-e-ystallization speed In
4OKh2N2M under the aotion of elements Cr and Mo originating carbide. For ea~fl
temperature existj a deformation degree beginning fr~,T- which the weakening
compensate the atrain-hardening processes. The deformat-4--n degree corresp:md-ng
to the maximum strain-hardening deoreases with !:.creasing tomperi*,irl: "*-- -31.
steels from 25-30% at 9000-C d-,wn to 10-15% at 1,200oC. An tn,:rea--'m in lh-
of elements Cr and Mo, crlglna+.ing carbide in the inve2tigatea --taels,
the hardenability of the steel as well as its defomaticn res:-zteznce. 7hArc- are
6 figures and 2 references.
Translator's note: This Is the full translation cf the nrigln-il Russian abstract.
Card 2/2

-M(5) /,A 9100 66736
AUTHORSt Leviting V. V., Sueloparov, G. D. SOV/20-129-2-22/66
TITLEt Electron Microscope and Electron Diffraction Pattern Studies of
Carbide Particles in Stainless Austenite Steel
PERIODICAM Doklady Akademii nauk SSSR, 1959t Vol 129, Nr 2, PP 318-320
(USSR)
ABSTRACT: The present paper deals with the distribution of carbide particles
in steel and their crystal structure. The steel used for the
investigation contained 0.09 % C; 17-7 % Crg 10.9 % Nit 1.2 % Mn,
0.2 % Big 0.022 % Po 0-014 % S. These samples were quenched in
water from 10500 and tampered at 600; 650; 700 and 7500 for two
hours. The specimens were blanched with a solution of bromine in
methanol with only the metallic bass having been dissobod. In this
treatment the carbides rose above the surface of the ground
section and maintained the position they occupied already in the
steel. The collodion prints with the "captured" particles were
evamined in an electron microscope for stereophotographs. Carbide
particles at the grain boundaries and a relief of the blanched
surface were investigated. The character of the carbide
Card 1/3 predipitates is almost unchanged along the entire boundary between

66'''Y,
Electron Microscope and Electron Diffraction SOV/20-129..2-22/66
Pattirn-Studies of Carbide Particles in Stainless Austenite Steel
two grainst there existq howeverp differences between the
individual boundaries, Dispersity decreases with decreasing temps
ture of tempering. In all cases the plane of the increase of the
particles agrees with the boundary between the grains. At
tempering temperatures of 600 and 6500 carbide precipitates were
observed not only at the boundaries but also within the grains.
The intergranularg much more dispersed particles are found where
the uniform orientation of the blanching patterns is disturbed.
The carbide particles had'the shape of two-dimensional dendrites
(20W4 cm to 7,1e4 cm long, maximum thickness of the order of
1076 cm). The point electron diffraction patterns which belong to
the lattice of the cubic carbide (Cr,F9)23C6 were used for
determining the orystallographical planes and the directione of
particle growth. The branches of different orders of the
dondritee of carbide belong, as a rulev to different planes for
the particle is formed due to a mosaic like growing together of
sonoorystals. The results of the determination of the planes and
of thurowth directions of the carbide partieles formed at 650
Card 2/3 and 7 are listed in a table. The angles be #een the dV~ons
V C
4 C

Electron Iticroscops and Electron Diffraction SOY/20-129-2-22/66
Pattern Studles of Carbido Particles In Stainless Austenite Steel
of the branches of growth and between the crystallographical
directions are in satisfactory agreement. All directions of growth
of the carbide particles are in those planes which belong to the
form fiool . in more than half of the cases the growth taken
place In parallel with [100] . The carbide particles grow along
the Intergranular boundaries since in these ranges the activation
energy of the decay of the oversaturated solution is reduced. At
the sites of the Intragranular disturbances of the crystal
structure of austenite higher dispersed particles are separated.
There are 2 figures, 1 table, and 6 references, 3 of which are
Soviet.
ASSOCIATIONs Ural'skiy nauchno-iosledovateltakly institut chernykh matallov
(Ural Scientific Research Institute for Ferrous Metals)
PRESENTED: July Gi, 1959, by N.V. Belovj, Academician
SUBMITTED3 July Is 1959
Card 3/3

Mli t3
pst
1"6 r
5!!1j
it
V I
ill g - i. I I I i - -
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RIX%

81878
8/129/60/000/08/005/009
B073/K135
AUTHORS: Levitin, V.V., and Syreyshchikova, V.I. (Engineers)
TITLEt Rejection of CarkidWat the Grain Boundarieg during
Tempering of Austenitic Steelot
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
19607 No 81 pp 20-25
TEXT: The work described in this paper was devoted to studying
the influence of small additions of various elements on the
character of rejection of carbides during tempering of austenitic
stainless steels and the stability of such steels against inter-
crystallite corrosion. For the investigation a nitrogen-
containing, chromium-manganese-nickel steel was chosen (0.09-
0 12% C- 16-18.6% Cr; 3.3-5.5% Ni; 6-9.5% Kn; 0.12-0-35% Ni
M;; 0.;1 Si, max 0 .01+% P? MaY. 0*03% S. After quenching from
1050 OC the mech4nical p&operties were as = 34-39 kg/mm2;
Ob = 73-79 kg/mm;2; 6 = 7~-53%; ak = 2tsk;m0/;10MW.t
The additions used for preventing rejection of carbides at the grain
boundaries and for preventing the tendency to inter-crystallite
corrosion can be subdivided into the following two groups:
Card 1/4

81878
S/129/60/000/08/005/009
H073/H135
Rejection of Carbides at the Grain Boundaries during Tempering of
Austenitie Steel
admixtures which combine with carbon to form strong carbides;
admixtures which reduce the excess energy of the inter-crystallite
transient zone. As elements of the first group the authors chose
Mo, Nb and Ta; as elements of the second group they chose Be, Cal
Ag, Ce and B. Grade A electrical ironv nitrided ferro-chromium,
low-carbon ferro-chromium and metallic manganese were chosen as
charge materials for the laboratory high-pressure furnace, whilst
carbide-forming elements were introduced into the steel in
quantities which are required for carbide formation. Other
additions were introduced in quantities between thousandths and a
tenth of one percent. The ingots were machined off to a depth of
3-5 mm and forged into rods from which specimens were cut out.
Specimens for micro investigations were heated in a salt bath to
temperatures between 950 and 1250 OC in steps of 50 OC for one hour
and then uenched in water. The tempering was by heating for two
hours at Z50 OC. In some cases additional tempering for 15 minutes
and two hours was carried out at 700 and 750 OC. The quenching
temperature at which the smallest quantity of carbides separated at
Card 2/4 0~

81878
B/129/60/000/08/005/009
9073/9135
Rejection of Carbides at the Grain Boundaries during Tempering of
Austenitic Steel
the boundaries was determined metallographieally. Following that,
specimens were treated according to this regime and used for
determining 'the tendency to inter-crystallite corrosion, which
was determined after boiling of the specimens in astandard
solution and inspecting the crack formation caused by subsequent
bending,and by measuring the increase in electrical resistance.
In some of the steels the carbide phase was separated
electrolytically in & saturated solution of sodium chloride which
was acidified by hydrochloric acid. The thus produced
precipitates were subjected to X-ray Analysis using cobalt
radiation. Six microstructure photographs of various steels
(without and with additions) after quenching and tempering at
650 OC for a duration of 2 hours are reproduced on p 21. The
results of Investigations of the tendency to develop inter-
crystallite corrosion after quenching and tempering at 650 OC are
entered In a Table on p 23 for steels from 26 heats. On the basis
of the obtained results the following conclusions are arrived at.
Rejection of the carbides during tempering of the investigated
Card 3/4 V1('

81878
S/129/60/000/08/005/009
B073/2135
Rejection of Carbides at the Grain Boundaries during Tempering of
Austenitic Steel
steels can be prevented by reducing the carbon content from 0.09-
0.12% to 0.04% and also by introducing molybdenum, niobium and
tantalum. The resistance to inter-crystallite corrosion during
tests in a standard solution is maintained In low carbon steel and
also in steel containing tantalum to an extent of 20 times the
carbon content. Addition of tungsten and also an increase in the
niobium content in excess of 10 times the carbon content leads to
ferrite formation. Berrylium accelerates the rejection of carbides
during tempering of hardened steel, whilst calcium, silver and
cerium do not influence this process within the range of
investigated quantities. Boron (0-003-0-10%) prevents the formation
of a carbide network in the case of tempering at 650 OC, but assists
such formation at more elevated temperatures. The influence of
boron depends on the quenching -temperature and on the carbon
content of the steel.
There are 1 figure, 1 table and 12 referencess 9 Soviet,
2 English and I German.
ASSOCIATIONs Urallskiy institut chernykh metallov
(Ural Institute for Ferrous Metals) V1(
Card 4/4

S/081/62/000/001/034/067
c) B102/B101
AUTHORS: Levitin, V. V., Syreyshchikova, V. 1.
C----------------
TITLE: Methods to prevent interaryotalline corrosion in stainless
austenitic steels containing nitrogen
PERIODICAL: Referativnyy zhurnal. Khimiyaq no. it 1962p 3071 abetract
11193 (Byul. nauohno-tekhn. inform. Urallskiy n.-i. in-t
chern. metallov, no. 8, ig6o, 62-67)
TEXT: Methods of preventing the tendency to intercrystalline corrosion in
N2'aontaining austenitic steels were investigated. These are based on
reducing the C content in the steel and on the adoption of carbide
developers which do not remove N2 from the solid solution. It was found
that the separation of Cr carbides in the drawing of austenitic Cr-Mn-Ni-
steels which contain N can be prevented by reducifig,, the C content in
such steels from C1.09-6-12 to 0,,04%.or by adding Mo, Nb or Ta to theme
EAbstraotorts note: Complete tranalation,3
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q/i.37/*61/ooo/1o12/i3o/i4q
A006/A101
AUTHORi V.V.
TIM$ Investigation of particles on grain boundaries of boron-containing
stainless stsels
MtIODICALt fleferativnyy zhurn&l. Mstallurgiya, no. 12, 1961, 12, abstract
12196 (*Byul. nauchno-tokhn. inform. Ural'skiy n.-i. in-t ohern .
metallov", 1960, no. 8, 74 . 77)
TMt Electron-mioroseopical and sleatronopaphical investigations were
made of iX18119 (lXhl8N9) and Xl7H4r8A (xhirOU) steel grades, containing
B. The specimens were water-quenahad from 1,100 C and.tempered at 600 - 750 0C.
It was established that when 0.0005% B was added, multiple dispersed carbide
partigles were formed on the grain boundaries, instead of relatively coarse (1-
7.10- cm) dendritio carbide particles (CrF*)2,C6- There are 8 references.
T. Fedorova
[Abstracter's notet Complete translation]
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S/137/61/000/011/095/123
A0601AI01
AU7HOR: I Levi
TIME: On the study of boron distribution In alloys by the method of neutrar
activation
PER13DI-CAL: Referativnyy zh,arnal. Metallurglya, no. 11, 1961p 36, abstract 1112,45
("Byul. nauchno-tekhn. Inform. Urallskiy n.-i. in-t chern. metallov",
ig6o, no. 8, 78-80)
An Investigation was carried out upon the boron distribution In Fe-b
and stainless steel. A liquld ermulsion A-2 was deposited by dipping upon micro-
sections, by the method worked out at the NIKFI. The specl ens were irradiated
by thermal neutrons; a Po-Be source with power of -3 * 10 neutrons/sec was
used. A nonuniform distribiition of B was noted in the Fe-B; In 3tainleSs steel
no zones of intorcrystal lite F3 absorption were discovered, apparently because of
their small thickness and Inaufficlent resolvIng power of' the ratilographic miethod.
(Abstracter's note: Complete translatIon]
0. Belyayeva
"ard 1/1

82645
S/126/60/010/02/017/020
E111/E352
AUTHOR: Levitin V.V.
TITLEs Influence of Boron on Diffusiondof IronVIin Austenitic
teals
PERIODICAL. Fizika metallov i metallovedeniyq 1960, Vol. lo,
No. 2, pp. 294-297
TEXT: In this letter to the editor the author reportshis study
by the tracer method of the influence of boron in stainless
austenitic steels on the diffusion coefficient of iron. For
measuring the activity of the integral residue he used the method
of Borisov et al (Ref. 6) which has advantages over that of Fisher.
Two steels, types IKhl8N9 and Khl7N4G8A, were used, respective
percentage compositions being OeO8, 0.08 C; 18.0. 17.5 Cri
9-3, 3.8 Ni; 1.2, 7.6 Mnl 0, 0.20 N; 0-20, 0-50 Si;
0-015, 0.012 P; 0.018, 0-013 S. One heat of the first steel
contained in addition 0-000510' B and one 0-00514' B; and of the
second 0.005 and 0.009% B. After annealing and forging
12 x 12 x 10 mm specimens were hardened to give a grain size of
19-22 and 25-26 IL, respectively, and a 2-6 4 thick layer of
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82645
S/126/60/010/02/017/020
EIP/E 12
Influence of Boron on Diffusion of OF n Austenite Steels
radioactive Fe59 was electrodeposited on a polished surface.
Figs. I and 2 show for lKhl8N9 and Khl7N4G8A steel, respect-
ively, plots of the ratio of specimen radioactivity after
removal of a layer of thickness y to its initial value
against y/2b , where b is the average grain size. Calculated
values of the diffusion coefficient and other diffusion
parameters are shown in Table 2, values calculated by Fisher's
method being shown in Table 3. For each steel the first
addition of boron produced a considerable influence, the next
comparatively little. The author has previously observed with
V.I. Syreyshchikova (Ref 11) that boron effects carbide-phase
precipitation kinetics; this is probably due to its offect on
diffusion. There are 3 tables and 11 references: 9 Soviet and
2 English.
ASSOCIATIONt Urallskiy nauchno-issledovatellskiy inatitut
chernykh metallov (Vral Scientific Research
Institute for Ferrous Metals)
SUBMITTED: April 3, 1960
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2'~ 0 0
21095
S/ 135/6 1/01:rV04 _- /007/011
A006/A 0 1
AUS"HORS: revitin, V. 'I.,_ and Platova, T. A., Ergineera
TITLE: The welding of stainless austenitic steels w!th reduced nicv~l
content
PER10DICAL: Svekrochnoye proizvodstvo, no. 5, 1961, 21-22)
TEXT: Previously, Investigations were made of auste.nltic s*.ainI65s, steels
with reduced content of nickel, alloyed with marganese and rAtroger. (Pef, 1-4) .
The authors of the present article stadied I.,. wAld g of IX17W4r8A OniviliGBA)
steel _zontainlrgi < 0. 12% C; 16.5 - 18.5% C1 , _~. - 5.5% NI; 6 Mn; 0. 12 -
0.24% N; -~' 0,6% SI; 73 kg./m2; OLn o,,- 9 kgm1cm
bending angle 1800. Satisfa6tory corrosion resistance of th.-i weld is Dtta!red
by welding with electrodes whose rods are made of OKh'L8N9 wire apd wi-ioze coitIngs
contain ferronioblum and ferromolybdentAm. ro assure satisfactory resls*,ance to
interorystalline corrosion In the heat affected zone, it is reconn~-r.Jed to -n'lin-
tain the carbon onitent In the steel nt a level not exceeding 0.0~%. 71-v~'re are
3 tables, 2 figures anJ 6 references: 4 Soviet and 1 n,~n-Sovlet.
ASSOCIATION: Urallskly lnstltut cherrykh metallov (Ural Inz".1lute of Ferrous
Metals)
Card 212

2 1 -1 11 9
1/0 11/()03/006/017
E 111 /E 4 3 5
AUTHOR; Levitin, V.V.
TITLEs Investigation of the Influence of Boron an
Decomposition of the Suparsaturated Solid Solution at
Grain Boundaries of AtAstenitic Alloys
PERIODICAL: Fizika metallov I metallovedenlye, 1961. Vol.11, No-3,
pp.392-399
TEXT: The precipitation of (Cr,Fs)-13C6 In austenitIc etainless
steel& is a typical example of solid-solution dez;ompositxon
stimulated by grain boujidaries. me present author with
G.D.Sualoparov (Ref.4) and other investigators , e.g. E.M.Kabla
and N.A.Nielsen (Ref.1), AJI.Kinzel (Ref.2), have studied the
nature of the decomposition products. It Was shown (Ref.4) that
the flat dendritic crystals grow An planes Loinciding with the
inter-grain boundaries of the wtrix phase; the dendrites branch
along those crystallographic direc?ions in the carbide lattice
which have the densest packing of carbon atoms. On the theory of
Intergranular Internal absorption (Ref.5) carbide fornkition at
grain boundaries should bt greatly affe.rxed by adsarption-active
impurities, including boron (Ref.6 - 13). Vic object of the
Card 1/5

S/1,46/61/011/003/006/017
Investigation of Eili/Eli35
present work was to study the effect of bor-Gri on the decomposition
of the supersaturated solid solution In intergrain junction zones
of austeniti. steels. Quantitative metallographic. electron-
microscopic and electron-diffraction methods were tised, Two
steels were used, melted tit a basic induction ftirnace.,. t ype
IX18H9 (lKhl8N9) M 0.08 C. 18.0 Cr, 9.3 Ni, 1.2 Mn, O~2 Si,
0-015 P, 0.018 S, zero, 0.005 or 0.0005 B) and X17AMA
(Khl7N4G8A) (%&0.08 C, 17-5 Cr. 13.8 Ni, 7.6 mn, 0 . 2 IN' 0.5 S1,
0.012 P, 0.013 S, zero, 0.005*4r OvO09 B). 16 kg Ingots were
forged into 12 x 12 mm bars. ' e ,fore hardening the specimens were
treated f or one hour in a a4 J kt1i and then tempered in a lead
bath. For each electrolytici'lly etched hardened polished section
the overal; lengtp of grain 6otiizdaries was determined by the random
intercept4#Nethoa*;tnd on'tempere'd' sections the boundary llngth was
detersainewVon which. 6Af -ip:Lta t ion had occurred, Vic efy~cA of
boron was as timated from the change tit the rativ vf theWt9.0
lengths whic"it Acurred when boron was oresent. Fig.1 shows for
l]Khl8N9 steel *the values of this ratio (length of grain boundaries
on which precipita1ion tins occurred to total grain-boundary length
EPK/'EP ) a& functions of the temperin,, temperature for hardening
Card U5

S/l'()A1/01l/003/oo6/ol7
Investigation of Ell~/E/135
from 950, 1100 and 1.200"C (graphs A, b ., and H retpectively) and
for boron contents of 0. 0.0005 and 0.005~u B (curves 1, 2 and
3 respectively). The corresponding graphs for Khl7N4G8A are
shown in Fig.2, the hardening temperatures here being io6o, lloo
and 11400C and the boron contents 0, 0,005 and 0,009%. For
both steels small bor-on additions lower the ratio when hardening
and tempering temperatures are relatively low.; with higher
boron contents and hardening and tempering temperatures,, the
ratio (i.e. the proportion of boundaries oczupied by the excess
phase) rises. Electron micrographs showed that In lKhl8N9 steel
without boron. tempered at 700~C for 2 hours, f"irly liirge dendrites
are formed at grain boundarie3z much fincr crystale in greater
numbers are formed when boron in Fresen~, Similar effez!ts are
observed with tempering at 650"C. for 50 minutes. Electron
diffraction results tnditate that th(i boundazy product In boron-
containing steel has the same cubic carbide lattice with the some
period (within the experimental error)j this applies to both
steels with the maximum boron content. Chemical analysis gave
indecisive results for lKhl8N9 steel but for Khl7NIiG8A steel,
Card 3/ 5

21219
Investigation of s/126/6i/oil/003/006/017
EIII/E435
hardened from the temperatures of 950 and 1100*C, a tendency for
the quantity of precipitat.ing phase to decrease under the influence
of boron waif observed. The author concludes that the observed
effects of boron are due to two sets of olopo3lng factors-
1) those reducing the excess energy of the intergranular zone and,
by reducing boundary diffusion, delaying decompcsition,
2) those increasing the degree of supersaturation of the solid
solution and thus accelerating decompa4ition, Ackmawledgments
are expressed to Professor V.I.Arkharov for his valuable
suggestions. There are 5 figures, 3 tables arid 20 references:
13 Soviet and 7 non-Soviet.
ASSOCIATIM Urallskiy nauchno-iasiodovatellakty Institut
thernykh metallov (Ural Scientific Research
Institute for Ferrous Metn1s)
SUBMITTED: August 22, 1960
Card 4/5

21363
14 Ii!)' 5/126/61/011/004/010/023
E073/E535
AUTHORi Levit1n. V. V~
TITLE, Influence of Small Boron Additions on the Low Tempers-
ture Impact Strength of Austenitic Steel
PERIODICAL: Fizika metallov i metallovedeniye, 1961, Vol.11, No.4,
PP. 564-567
TEXT. Decomposition of the saturated solid solution at the
grain boundaries of austenitic xtainless steel does not lead to a
drop in plasticity at normal temperatures but it leads to brittle
fracture at sub-zero temperatures. Small additions of boron have
a great influence on the process of decomposition of solid
solutions in austenitic steels and.- therefore, they should also
influence the process of impact fratture at low temperatures- The
inves-tigations were made on Cr-Ni steel containing 0,08% C,
18.0% Cr, 9.3% Ni, 1,2% Mn, 0.2% Si; 0.015% P and 0.018% S_
0,0005 and 0.005% boron were introduced in the second and third
ingots and,from the forged rods,specimens 10 x 10 x 55 mm were cut
out. The heat treatment consisted of quenching from 950. 1100 and
1200'C followed by tempering in the range 600 to 750'C. After
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influence of Small Boron S/126/61/011/oo4/010/023
E073/E535
heat treatment a V-shaped notch with a depth of 2 mm and an angle
of 6' was cut on one side of the specimens and these were then
soaked in liquid nitrogen and tested on an impact test machine
having an impact load of 18 kgm~ On a part of the specimens the
magnetic induction after 20 min holding in liquid nitrogen was
measured prior to making the notch. The results show that the
impact strength of austenitic chromium nickel steel,aftei two
hours tempering,le sharply reduced at the liquid nitrogen tempera-
ture. The steel is prone to brittle fracture, which appears to be
intercrystalline, Introduction of small quantities of boron
brings about an Increase in the impact strength from 1.6-4.5 to
6.8-12.0 kgm/cm2 and this favourable influence is sustained for all
the Investigated quenching and tempering temperatures. An
increase of the tempering duration to 100 and 500 hours will lead
to embrittlement of the boron containing steels but the impact
strength will still be somewhat higher than it is for steel of the
same composition without boron. 2Graphs, Fig.3, were also plotted
of the impact strength, ak kgm/cm , as a function of the
induction,.B, Gauss. it can be seen that with increasing
induction, I.,e., with increasing content of the magnetic phase in
Card 2/4
R"'-. R'D
i .4r.! . - IN,

Influence of Small Boron S/126/61/011/004/010/023
E073/E535
the specimen there in indeed a decrease in the impact strength.
However, the measured induction, determined by the total quantity
~of the a-phase, is not an unequivocal function of the impact
strength. The plot,'Pig.3a, applies to steel without boron, the
plot 6 applies to steel with 0.0005% boron, the plot 6 applies, to
steel with 0.005% boron. Heat treatment regimes were as follows
(see symbols in the figure): 1 - 6000C, 2 hours; 2 - 6000C, 100 hours;
3 - 6oo*C, 500 hours; 4 - 650*C, 2 hours; 5 - 650*C, 100 bours.;
;6 - 6500C, 500 hours; 7 - 7000C, 2 hours; 8 - 7500C, 2 hours.
In boron-containing steels small particles of the cold britttle
ferrite ifill be p?resent instead of large branchings of this ferrite.
~However, long duration tempering leads to an increase in the
size of these particles and thus to a decrease in impact strength.
There are 3 figures, 2 tables and 4 references: 3 Soviet and
I non-Soviet.
ASSOCIATION: Ural'skiy nauclino-issledovatellslciy institut
chernylth metallov (Urat Scientific Research Institute
for Ferrous Metals)
SUBMITTED: August 22, 1960
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I;TIIOIZS:
TITI.r.:
S/126/62/013/001/007/018
EIII/E580
Lqvitin- V-Y. and Tanannyova, A.N.
Contribtition to the theory of the in tergrantilnr
corrosion of stainless steels
JILRIODICAL., Fizika metallov i metallovedeniye, v-13, no.1, 1962,
T%XT: The most widely accepted theory of the susceptibility
of nustenitic stainless steels to intergranular corrosion is based
on the idea that solid-solittion zones adjacent to the precipitated
carbide phase are impoverished In chromium. The present work
attempts to prove experimentally this theory. The method was based
on the difference between tho electrode potentials of the
impoverished zone and solid solution (Ref-13: Schafmoister P.
Arch. EisenhUttenw., 1937, 10, 405) under intergrnnular-corrosion
test conditions. The avorage thickness h of the zone in given
(thotigh not very accitrately) byl
- P
cdS1,2: L
where P in the weight of dinsolved chromium, c the average
Card 1/3

Contribution to the theory of ... S/126/62/013/001/007/018
Elli/E580
concentration, d the density, S the surface of the specimen, 6 tile
depth (small compared with specimen size) of corrosion penentration,
the area of intergranular boundary per unit voltime of specimens
Specimens 9 x 9 x 10 min were machined from 12 x 12 mm rorg#-.d bars of
type V19HQ (naitiI.Ng) steel (o.o8;j c, 18.0~'i Cr, 9.3% Ivi, Mri,
0. 'J -in(] teiripering
20~ Si, 0-015',' P and 0.018' S). After hardening ,
each specimen was polished with emery, weighed and refluxed for
24, 118 or 72 hours in 110 ml of a solution of 51 ml 11 SOf and
110 ml CuSOI,.511.0 per litre water. Iron, chromium aiid hickel
were determined calorimetrically, .1 metallogrnphically and ZL by
the random-intercepts metholl. h was fotind to be 950-1130 A J'or
48 hours treatment and depended little on tempering teriperatitre,
After 72 hours treatment h became qlo-lio6o A. The latter is
attributed to the greater distaiice between carbide particle.-4 aild
zones with more chromium. Although this investigntion cotifirms
the impoverishment theory, the authors note that this doe!4 ivot
excltide the likelihood of other factors mnking steel liable to
intergranulnr corrosioii. There are I figure an(] 3 tables.
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Coritril)tjtion to tbe theory of ... S/126/62/013/()01/007/018
El I 1/E5110
1SWC1 ATION: 11rallmkiy iiisititut cheritykh metAllov
(Urnl Institute of Ferrous Metals)
5111NITTE'D: may io, ig6i
Card 3/3
36597
5/126/62/013/003/001)/023
E091/Zl33
:'AUTHORS$ Syreyshchikova, V.I., Levit4gL._V.V., and
Farafonov, V.K.
TITLZs On the influence of grain size of austenitic steels-
on their refractoriness and nature of fracture in
creep
PERIODICALs Fizika metallov i metallovedeniyog V.13, no.3,
1962. 394-398
TEXTs The influence of grain size and the properties of
,grains of varying dimensions in forgings of steel 3A612 K
AE1612K), with respect to refractoriness and nature of cracks at
650 and 700 OC was studied. The chemical composition of this
7steel (in-1h) in as follows: 0,-09 C; 0.34 Si; 1*19 Mn;
115.0 Cr; 36.5 Ni; 1,5 Ti; 3.2 W; 4.1 Col 0,012 B; 0.013 P;
10-004 S. An ingot 2.1 tons in weight was forged into a rod of
300 mm diameter. The forging was cut into longitudinal templets
of 20 mm thickness. Specimen billets were cut from peripheral
.portions of the latter, in order to exclude the influence of
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On the influence of grain size ... S/126/62/013/003/009/023
E091/ZI35
,defects in the central zone. The templets were soaked at 1200 OC
for 2 hours and quenched. They were then ground on two opposite
sides and etched in order to expose the nature and size
,distribution of the grains. Etching was carried out at room
temperature in a solution consisting of a mixture of 20 weight
parts of hydrochloric, 10 parts of nitric acid, and one part of
potassium dichromate. The average grain size on the surface of
~billets of 20 x 20 mm cross section was determined by measuring
the diameter of 200 grains. Selected billets were tempered in
three stagess at 850 OC for 10 hours; at 700 OC for 20 houral
and at 65o OC for 30 hours. For the purpose of testing for
refractoriness, specimens of 10 mm diameter and 100 mm working
.length were cut from the billets. The tests were carried out at
700 OC at loads of 22 and 18 kg/mm2, and at 650 OC at loads of
,30 and 26 kg/mm2. Four specimens with various grain characteria
tics were tested for each load. The surfaces of the specimens
after failure and their fractures were studied both visually and
with the aid of a 'jinocular microscope. Sections for
metallographic study were made in the axial plane of the specimens.
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on the influence of grain size ... S/126/62/013/003/oug/023
E091/E135
These were polished electrolytically and etched in a sulphuric-
phosphoric-chromic electrolyte. It was found that creep occurs
under the above conditions both by viscous flow along inter-
crystalline boundaries and by slip within the grains. During
deformation, internal cracks develop along intercrystalline
boundaries in the specimens in a direction perpendicular to the
applied load. Large grains lying in the path of cracks so an to
oppose their propagation perpendicular to the specimen axis,
temporarily retard their spreading. No strengthening occurst
however, since failure develops further due to the formation of
intercrystalline cracks in other places. The large grainal
having stopped propagation of the cracks, are stress-relieved by
slip, probably after they have rotated somewhat into a more
favourable position. Vacancies accumulate along the slip planes,
cracks form and cleavage occurs, Under the conditions
investigated, failure occurs along the most closely packed
planes of the type (111). The nature of failure (intra- or
inter-crystalline) is determined 'essentially by the grain size
in the specimen cross-section. An the grain size increases, the
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On the influence of grain size S/126/62/013/003/009/023
E091/E135
development of intercrystalline cracks becomes more difficult
and the destruction acquires an intracrystalline chaiacter.
So long an the grain size is small as compared with the diameter
of the specimen, the stability of the latter does not decrease.
In specimens, the cross section of which contain large grains
(3-5 mm) comparable with the diameter of the specimen, cleavage
At: in the large grains drastically weakens the cross section, an a
result of which the ape'cimen fails quite rapidly. Regions
containing small, as well as large, grains exhibit different
plastic properties, owing to localized predomination of different
mechanisms of deformation. These result in the appearance of
deflecting loads at the boundaries between these regions, which
decrease the stability, There are 4 figures and 2 tables*
Card

S/126/62/013/003/009/023
On the influence of grain size ... E091/El35
ASSOCIATIONt Urallskiy nauchno-issiodovateltakiy Institut
chernykh metallov
(Ural Scientific Research Institute of Ferrous
metals)
Institut. tyazhelogo mashinostroyeniya pri UZTM
(Institute of Heavy Machinery at*UZTM)
SUBMITTEDs Initially, June 5. 1961, and
after revision, July 10, 1961.
Card 5/5
MIT MIM

S/126/62/014/001/015/018
E07l/El35
AUTHORS: _L!yjjin_-V-~ and Syreyshchikova, V.I.
TITLE: An investigation of the strengthening phase of a
complexly alloyed steel 3K6l2Y- (Ei 612K)
PERIODICAL: Fizika metallov i metallovedeniye, v.14, no.1, 1962,
144-146
TEXT: The form of crystallites, structure and composition of
the phase which separates during ageing and during retention under
load were studied for the steel EI 612K. This steel, after
hardening and ageing, possesses properties which are high for
austenitic class steels. Electron microscopy and electron
radiography studies and chemical analysis were ma7de of the isolated
phase of specimens cut out from an ingot containing: 0.09;6 C;
'/ Ni; 4.1% Co; 3.2% W; 1-5% Til 0,18~4 Al; 0.012% B;
15.0;~ Cr; 36.550
1.2V7 Mn; 0.3C~ Si; 0.013% P; 0.004% S. The specimens were
hardened from 1200 *C and annealed in three stages: 850 *C -
10 hours; 700,*C - 20 hours; 650 *C - 30 hours. For the heat
resistan'be tests specimens with a gauge length of 100 mm, 10 mm
in diameter, were used. The phase, separating.on ageing, is so
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S/126/62/olVooi/m/018
An investigation of the ... E071/EI35
highly disperseld that an optical microscope could not be used for
its study. This phase has a cubic face centred lattice with a
period a = 3.59 A- Apparently, the phase represents a solid
solution based on intermetallic compound N13AI. The phase -
Ni3(A(,Ti) with a face centred cubic lattice (referred to as a'-
phase in Soviet literature) was observed in nickel baapd alloys..
The chemical composition of the phase could not be-established
accurately. It contained mainly Ni, Ael Ti and small quantities
of Fe and Cr but no Co or W. On increasing the time of retention
under load to a few thousand hours, the phase in enriched in
titanium, whereupon the ratio of atomic concentrations of
titanium and aluminium increases from 0.9 to 2. There in 1 figure.
ASSOCIATION$ Ural'skiy nauchno-inaledovateltakiy inatitut
chernykh mdtallov (Ural Scientific Research Institute
of Ferrous Metals)*
3UBMXTT2Ds Febru^ry 13, 1962
Card 2/2

SYREYSHCHINOVA, V.I.; lMT~Aj_Y.V.j FARAFONOV, V.K.
Investigating proresses of hardening, creep, and rupture of austnnit.te
steel. 1831. po zharoproch. splav. 10:116-123 163. (MIRA l7s2)

S/126/63/015/003/005/025
E021/E135
AUTHORS: Syreyshchikova~ V.I. , and Levit in, VO V..i
TITLE: Investigation of intra-granular structure of
austenitic steel after fracture during creep
PERIODICALt Fizika metallov i metallovedeniye, v.15, no.3* 1963,
352-356
TEXT: The authors have previously shown that in type 3V1612K
(E1612K) complex-alloyed heat-resisting steel the development of
inter-crystallite cracks during high-temperature deformation is
hindered and the fracture acculires an intra-granular character.
The aim of the present work was to study the creep mechanism of
this steel by investigating the intra-crystallite cleavage planes
and grains in the axial part or the specimens after fracture.
Fracture temperatures were 650 and 700 *C. Fractures wore studied
by back-reflection X-ray and microscopic methods. The results
showed that with comparatively brief tests At 650 *C individual
large grains fracture along slip planes (like single crystals).
The plane of easiest slip is the ~1111- plane of the austenite
lattice. With increasing test tiw~ and temperature the importance
card 1/2

S/126/63/015/003/005/025
Investigation of intra-granular E021/E135
-,of inter-granular flow increases and elastic bending of individual
cryntallites can occur. The relaxation of stress in these
cryatallites occurs through their breakdown into aub-grains, the
extent of fragmentation increasing with increasing proximity of
the given grain to the fracture zone. It appears that insufficient
importance has previously been attributed to fragmentation, as a
particular case of polygonization, in creep; this process needs
further study. The mechanism of the intra-crystallite fracture of
the grain undergoing fr.-igmentation has not been explained: the
intra-crystallite crack may successively 'Jump' from one sub-grain
to the next, following changes in the orientation of the crystallo-
graphic plane; it is not impossible, however, that the intra-
crystallite crack proceeds along sub-grain boundaries.
There are 4 figures and 1 table. I
ASSOCIATION: Urallskiy institut chernykh.metallov
(Ural:, Institute or Ferrous Metals)
SUBMITTED., July 11, 1962
Card 2/2

ACCESSION NR: AT4013936 B/2659/63/010/000/0116/0123
AUTIIORI Sy*royshchikova, V. I.; Lovitin, V. V.; Farafonov, K. K.
TITLE: Investigation of strengthening, creep and failure processes In austenite steel
SOURCE: ANSSSR* Institut metallurgH. Issledovanlya po zharoprochny*m splavam, v.
10, 1903, 116-123
TOPIC TAGS: steel strengthening, steel creep, steel failure, austenite steel, steel plastic
deformation, polygonization
ABSTRACT: The process of failure under creep was previously Investigated for nonferrous
metals, but only a few analyses have been made of heterogeneous alloys. This paper des-
cribes the Investigation of the strengthening phase of a complex austenite steel alloy and
studies the plastic deformation and failure of this steel under creep conditions. Ile
influence of grain size on beat resistance was also investigated. The testing procedure
was carried out on an IP-4M machine. Ingots of2. 1 tons were fastened to rods 300 mm. in
diameter. :rhey were then hardened and tempered (860C for 10 hours, 700C for 20 hours$
and 650C for 30 hours). High-tomperature samples were cut from blanits with
Card 2A

ACCESSION UR: AT4013936
different sized grains. The samples had a diameter of 10 mm and a working length
of 100 mm at temperatures of 650C and 700C. Data on sample failure is tabulated. x
Samples containing relatively coarse grains (2-5mm) in a section with uniform grains
.(0, 15-0. 25 mm) were -the weakest. 7be strongest samples had sections with uniform
grains of 0. 2-1. 0 mm. FinaIly X-ray studies of failure under creep revealed polygon-
ization. Orig. art. hajcS figures and 2 tables.
ASSOCIATIONt Institut metallurgil AN SSSR (Institute of Metallurgy AN SSSR)
SUMMED: 00 DATE ACQ: Mob" ENCL: 00
MB COM M NO RLT BOVt 007 OTHM 001
2/2
~q W_-
S

ACCESSION NR., AP4038900 S/0114/64/000/005/0034/0036
AUTHOR: Blyum, ts E. (Engineer); Levitin, V. V. (Candidate of physico-
mathematical sciences)
TITLE: Stainless steel resistance to cavitation damage and #and erosion
SOURCE: Eno rgornashinostroyeniye, no. 5. 1964, 34-36
TOPIC TAGS: steel, stainless steel, cavitation, cavitation resistance, erosion,
sand erosion, sand erosion resistance, turbine, hydraulic turbine
ABSTRACT: An experimental investigation of the resistance of austenitic steels
Khl7N4G8A and (stainless) lKhl8N9 to cavitation and to wear by sand-water pulp
is reportedo The Khl7N4G8A steel has 2- 2. 5 times less Ni and a considerably
higher strength than the stainless steolo The cavitation resistance was tested on
an impact-erosion outfit in which specimens fastened to a rotating disk cut &
water jet in the cavitation zone (see Zavodakaya laboratoriya, 1954. no. 6).
Card

ACCESSION NR: AP4038900
After 8 hro of testing, the stainless steef was found to have serious cavitation
damage with pits up to 4-mm deep; the Khl7N4G8A steel developed cavitation pits
only after 26 hra. Sand-wear resistance was tested in a centrifugal-jet bowl
device where other steals (2x 13, 4x 13, St 35, Khl5N9Yu. 30KhGSA) were also
simultaneously tooted. ZKhl3. 4Khl3, and Khl7N4GBA proved to be the most
wear-resistant, and 30KhGSA the least resistant. Further wear-resistance tests
included the 330-hr sand-water operation of an R015GM84 hydraulic turbine in
whose guide case 4 blades were made from stainless steel and 6 blades from
Khl7N4G8A steel: the wear resistance of the latter steel proved to be 1. Z-1. 4
times as high as that of the stainless steel. Orig. art. has: 5 figures and
Z tables.
ASSOCIATION., none
SU;3MITTED: 00
SUB CODE: MIA
Card Z/Z
DATE ACQ: 053un64 ENCL: 00
NO REF SOV: 010 OTHER: OOZ

L ~-270,~-bb Wr k a ;,' T/_v6W,1% tLT I1,JPk-- ;, J, -nf D -1
ACC NR& AP6014424 SODRCE CODE2 'UR/0381/65/000/005/0057/0061
AUTHORSs -Rachok, A. Ta-.; Levitin, Vo V.; Kovalonko, N. K.
ORO: Ukrainian Scientific Research Institute for Special Stools, AUM and Ferro
Allus, Zoporoahe (Ukrainskly nauchno-ionledovatellskiy inatltut spetsiallzWkh
etaloyp ap-larov i forroaplavov)
TITIEs The influence of the depth or the decarbonized,layer In ball-bearing steel
on the total resistance of an induction coil
SOURCEt Dofektookoplyap no. 5# 1965# 57-61
TOPIC TAGS: steelp alloy steel,, metallurgic testing machine / ShKhl5 stool
ABSTRACTs The of at of the depth of the docarbonized layer in objects made from
cold-drawn SM151,14tool, on the total resistance of an induoti6n coil was determined,
A schematio of the experimental installation is presented. The experimental results
are presented graphically (see Fig. 1). It is shown that the depth of the decar-
bonized layer in stools may be successfully controlled by the method of eddy cur-
rents. Control was performed in the calibration shop of Dneprospetastall factory
My Yefremenko parties.-%tinge
with V. Me Belot and So .4
UDCt

L 32703-66
ACC NR& APWII,44 0
Fig. 1. Influence of the depth of the derarbonized
layer on the total resistance of the meas-
uring induction coil for the frequency range
50-6W cycles. Depth of dooarbonizationt
open circles - 0; crosaws - 0*09 im;
black circles - 0,21 mma (A) LIO LO - total
r0dativo r"istancel Rir/4)% contributed
active resistance by the aoil:4
Orige art* bass I table and 3 grapbse Ix
suB coms n,13/ SUBM DATEs 26;m365/ ORM M 002

STREYSHCHIKOVA VJ.i~,FVITIN 7.V. N-YUM, FJ:., KRUSNUMOV, K,Ij.
Effect of the meLhods of s.2elt.ing and heat treattent. on the
hept resistant propercleil of boiler pipe of 12KhIIOY and
l5KhlM3Y steel. Stall 25 no.4051-354 AP 165.
(MIPA 18111)
1. Drallskiy nauchno-Issledovatell3kly Institut chernykh
me Wlo-r.

-41:4
"k t ;/
ACC INKi A116027791 QN) SOURCE CODE: U11/0126/66/022/001/0101/0107
AU71110R. Levitin, V. V.; Yorshova, L. S.
ORG: Ukrainian Scientific Research Institute of Special Stools, Alloys and Forroalloys
(Ukrai~slldj AM -spotsial Inyk-h sta-Icy, - splavov i ferrosplavov)
TITLE: X-ray analysis of the effect of deformation and annealing on the structure of mono-
crystal specimens of a high7jtomjLpraturo alloy
SOURCE: Fizika motallov i metallovedcniyo, v. 22, no. 1, 1966, 101-107
TOPIC TAGS: high temperature alloy, crystal structure analysis, x ray diffraction analysis,
polygonization development / XhN77TYuR high-tcmperaturc alloy
ABSTRACT: Methods of x-ray diffraction topography and measurement of refleCtion intensity
were used to investigate the structuro of monocrystal specimens of I