SCIENTIFIC ABSTRACT SOKOLINSKIY, YE.A. - SOKOLKOV, YE.N.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001651930001-5
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 26, 2000
• Sequence Number: 1
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

L 8782-66
ACC NR: AP5028141
the oscillator average frequency; these changes are oscillatory. The envelopes
of these changes can be described by Bessel functions of the product of the line
electrical length and the frequency deviation. These effects increase with the
degree of mismatch and with the decrease in the line attenuation, the directivity
of the coupler, and the electrical length of the oscillation loop. Orig. art. has;
4 figures and 38 formulas.
SUB CODE: 09 SUBM DATE: 16Dec64 ORIG REF: 003
jW

L:C~e C-11twe - &.Iui~rlent. and Supplies
3live screen. ~~chel3vol',stvo, 29, Ilo. "I 1S:,5".
Monthl List of Russian Accessions, Library of Congress, Octoley- 1~62 IM, Uncl.

POSTNOV. G.A.; UFIMOV, O.N.; MILKYEV, V.S.; SOKOLINSKIY, Ys.A.
- ---.
Observations of Mars in 1950. BiuI.VAGO no.12:12-15 '53.
(KLRA 7-3)
1. Moskovskoye otdeleniye VAGO, otdel planet i luny.
(Mars (Planet))

ACC NR, AP7002978 SOURCE CODE: UR/0413/66/000/024/0077/0077
INVE'NTOR: Veksler, B. Ye; Katkov, G. F.; 14alinskiy, S. A.; Minkin, ME. M.,
Remonnikov, V. S. ; Rybakov, L. A. ; Sokolinskiy, Ye. A. ; Fedorov, V. N. ; Shmulovich,
1. Sh.; Gertsov, S. M.; Pishchulin-I-V. V.
OFG: None
T 1 -_'~'. A sLismic prospecting station. class 42, IN0. 18959a
SOITRCE: Izobreterd'ya, pro;nyshlennTie obraztsy, tovarnyye znaki, no. 24v 19662 77
~OF:C TAGS: seismic prospecting, frequency divider, quartz crystal, seismologic
s ta-, I c.. I
Ai3STRAM This Author's Certificate introduces a seismic prospecting station contain-
an wnplification-conversion channel, registration unit and rower supply. Tne
tin. i ned for improved reliability and operational convenience. A quartz os-
's desiF
cillator vith a frequency divider system is used as a precision-frequency power supply
and synchronizing unit. The oscillator is connected through amplifiers to the actua-
ting units of the station.
SUB CODE: 08 Sum DATE: o4jun65
Card UDC; 550-340-19

V 7.r
j
of
y
rLo -
C
0, Cr inr,
Pz L
rc')roductiorl
an'
-3aper, a re r
ty -,rans I c -6
C; -.0 -L-od of
acmad sil-altros of dinff, ampl:.fier
3:nd 0 uae racord
U D. c 550-340o',9-.

a_,-, CorL~ -n ;C)r4LI
a
7--30 liz, amn d oof 07,01---
cuto,,.,
Yo u roliall of trc rocorded
.1
nz.
Lrtc,,d di tccctioxA roception, -- nuitchin-
ja,-.t-~Ioci Of rc!-,-al -L u
=it re
-x) a "..t."t~c Cor-coction Unit" caid a =rdw,
maolotic di-Ll--,,, rccozdcr tlac reproduction a r.
-with t1he mothod of
rc,~u.~nc,.r selocz-on un-t is comocted b c. t7re ell
a:-.d t1le c uJr- recorder. To i7anrove tlie
a-.-, olc;cti-on bea~a for in-v--oducinz static and
cc-uod the reproduction azLplifier and 'he drum wita
coy-,.n L 1.

SOKOLINSKIY, Yu.A.
Calculation of the equilibrium of ammonia synthesis with the
aid of computers. KhL-i.prom. no.6:410-4-13 Je 162. (NaRA 15:1.1)
(Ammonia) (Chemical equilibrium)

SOKOLINSKIY, Yu.A.
I ------ --
Distribution of con'~entrations and tempera,'Cure in hetero-
geneous cataly-tic exchange reactors with inner heat exchange.
Kin. i kat. 4 no.6:910-918 Nm-D '63. (MIR-A 17:1)
1. Moskovskiy institut khimicleskogo mashinastroyeniya.

SOKOLINSKIY, 'Yu,A.
Design of catualytic reactors with interral heat trar!3fer.
Trudy MUM 26:161-173 '64. (~q,?A " '-';

.717
5'V,*

O.S.; PLANOTil".11', ': ~.~~;,!NSKTY, Yu.A.
CIIEKIIOVII , .." i -
Accounting for liquid m:xiig in the calculation of irAss exchange
plate columns. Khim., prom. 40 no.10:768-772 0 164. (MIRA 18~3)

USER/Engineering
Card 1/1 : Pub. 128 - 29/38
Authors t Konson., A. S-,,; Bugakov, M. Sh.; and Sokolitsyn., S. A.
Title i On accurate methods of calculating material requirements
Periodical I Vest, mash. 92 83-912 Sep 1954
Abstract : A critical review is presented of V. D. Lavrov's article published in
"Vest. mash. 12., 195211 on, "Progressive Methods for Calculating Material
Requirements in Part Production". Tables; graph.
Institution % *****
Submitted : #*see

SOKOLITSYN, S.A,
Calculating turnover stocks of materials needed for regular flow
of production. T-.udv LPI no.186:69-80 '56. (MLRA 10:?)
(Machinery industr7)

FBASE I BWK 70a
10.1mov. Aleksey Nikolayevich and Sokolitsyn, Sergey Alekseyevlich., Candidates
of Tecbnical S----!e=es
Pat'- obespecheniya ritmichnoy raboty promysh-lemogo predpriyatiya (Ways of
Ensuring Ballanced Operations in an Inchistrial Establisbment) Leningrad,
1957. 52 P. 3,050 copies printed.
Sponsoring Agency: Obshchestvo po rasprostranen-tyu politichesIdIch i nauchnykh
znan-iy RSFSR. Leningradskoye otdelen-1ye.
Ed.: Karlik, Ye. M., Candidate of Economic Sciences, Docent.; Ed. of
Pablishlag House: Savraskin,, A. G.; Tech. Ed.: Gurdzhiyeva~ A. M.
RMICGE: Th' s pamphlet is i-ntended to acquaf-rt . the reader with the progress
made Irj -re-rious sectors of So-riet industcl'y in the development of a balancea
and =iform rate of production.
COIMWE: This pamphlet reviews scme of the o=gaUizwtio,-mI- measures employed
by plants of the Soviet machinery indust--y to develop and assure balanced
Caa-d 1/P

lde;-js of Ensuring Balanced Opera-,' tions ( Con t. 702
opr--L~-a.-ioa and a uni orm ratee of production. There are 7 Soviet references.
No persa-w-lities are mentioned.
TAME CIF
CONTOTS: The Significance of IMices of WAnced Operation " a
U,niform Rate of Production 3
organizing the Production Process for Balanced Operation
and a Uniform Rate of Production 18
Organizing Operational and Production Plarm"ing for
Balanced Mass Production 32
Bibliography 52
AVAILABLE: Library of Congress (T58.K48)
C,-.rd 2/2 JG/aak
10-9-58

L
25(5) PHASE I BOOK EXPLOITATION SOV/2393
Leningrad. Politekhnicheskiy institut
Mashinostroyeniye; ekonomika, organtzatsiya i planirovaniye
proizvodstva (Machinery Manufacturing; Economics, Organization
and Planning of Production) Moscow, Mashgiz, 1958. 110 p.
(Series: Its: Trudy, Nr 200) Errata slip inserted. 2,800.
copies printed.
Sponsoring Agency: USSR,Ministerstvo vysshego obrazovaniya.
Resp. Ed.: V.S. Smirnov, Doctor of Technical Sciences, Professor;
Eds.: Ye. M. Karlik, Candidatei of Economic Sciences, Docent;
and S.A. Sokolitsyn, Candidate of Technical Sciences, Docent;
Tech. Ed.: R.G. Pollskaya.
PURPOSE: This collection of articles is intended for engineering
and technical personn~.-l*of machine-manufacturing establishments.
COVERAGE: This collection covers the theoretical aspects of the
Card 1/4

Machinery Manufacturing; (Cont.) SOV/2393
economics, organization, and planning of production and the
actual operation of machine-manufacturing t9tablishments.
The first five articles deal with problems of classifying
production lines for lot production, variations of the flow
of lots of parts, and duration of the machining cycle, etc.
The remaining articles are devoted to the economic efficiency
of new technology, problems of quality control, and to the
question of specialization and cooperation. No personalitries
are mentioned. Heferences are given at the end of several
articles.
TABLE OF CONTENTS:
Foreword
3
OlIkhov, G.A. Classification of Continous Machining Lines ~or
Lot Production 7
Klimov, A.N. Data on the Organization of Line Production of
Small Steam Boilers 16
Card 2/ 4

Machinery Manufacturing; (Cont.) SOV/2393
Titova, M.V. Organizing Quality Control of Parts Manufactured
on Automatic Lathes 90
Karlik, M., and G.V. Malakhovskiy. Specialization and Coop-
eration in the Iron-casting Industry in the Leningrad Economic
Region 96
AVAILABLE: Library of Congress
JG/ec
Card'4/4 1o-16-59

25(5) PHASE I BOOK EXPLOITATION SOV11212
Potochnyye metody proizvodstva v seriynom mashinostroyenii i
priborostroyenii (Assembly-line Methods in Serial Manufacturing
of Machinery and Tools) Moscow, Mashgiz, 1958. 325 P. 3*000
copies printed.
Eds.: Berman, A.G., Candidate of Economic Sciences,-and Neymark, A.I..',
Candidate of Technical Sciences; Eds. of Publishing House:
Varkovetskaya, A.I., and Chfas, M.L.; Tech. Ed.: Sokolova, L.V.;
Managing Ed. for Literature on Technical Machine Building (Leningrad
Division, Mashgiz): Naumov, Ye. P.
PURPOSE: This book is intended for production managers, dispatchers,
and engineering personnel engaged in the production of machinery
and instruments. It may also be useful to scientific workers,
planning personnel, and vtuz students specializing'in industrial
engineering.
Card, 1/8

Assembly-line Methods in Serial Manufacturing (Cont.) SOV/1212
COVERAGE: The book contains background material for the 1958
Conference an Methods of Line Production scheduled under the
auspices of the Committee on Production Organization of the
Leningrad regional administration NTO of the machinery manufacturing
industry. The Committee's recommendation for this Conference was
prompted by the inadequate development of line production methods
and techniques in Leningrad plants specializing in series [large-
scale] production of machinery and instruments. Theoretical
studies based on Soviet industrial practices are presented in
Part I of this book. Part II discusses the introduction and
development of line production methods in Leningrad plants while
Part III reviews foreign literature and some of the more pertinent
problems of line production as Been by foreign authors. There are
no references.
TABLE OF CONTENTS:
Foreword
3
Card 2/ 8

Assemb.l.y.-111--r- Mz~ I- !-,,-,Js ITI Serial Manufacturing (Cont.) SOV/1212
PART ONE. BASIC PROBLEMS OF CALCULATING AND
ORGANIZING LINE PRODUCTION IN SERIES [LOT]
MACHINER7 AND INSTRUMENT 14ANITACTURING
Ch. I. Organizatior .1 Forms of Production Line Processes and
Their F~_at",;:res. ( 0.1. Neporeat, Professor) 7
1. Organizaticrial and technical structure of the flow process 8
2. [P-roduct-1cn) prr,,,ess and t.,hyti,
I m 9
3. Featairv!s c~~' pvod!,v~-rlon pr--3cesses 12
14. Q-aalltativ-i! fl-ow (distribution) of worked pieces and its
signifi_,a.~'.,I-;,~, In ~-..rganizing the production processes 12
5. Organd.z.LPIg ItIrr--duction] pro-2esses In an area (production
I'1r.es) 13
6. orgs.-niz-ationa-i. forms of production line processes 14
7. Seq-u~_--Ice -cf start-Ing parts on a multiproduct line 22
Ch. II. Bas--l.o. Line Variants (A.!. Neym-ark, Candidate
26
Card 3/8

s oV/.*L2 12

26
33

lines 43
45
57
a general
65
Development
in
~'ate cf
d
69

p
I-S
g
70

73

A~qaemb'ly-!-ir- !.n Serial Manufacturing (Cont.) SOV/1212
Ch. IV. BasIc Frc~,blems In Calculating and Planning Production
blyips i.n MachInery and Instrument Manufacturing (A.I.
Nr-pm--i-r-k ', Cand-i-date of Technical Sciences) 86
Cal,3ulatIng single product continuous movement lines 86
2. Ca1cu.1arlng slngle product intermittent movement (direct
flow) --izines 99
3. Cair;-ulatu-jng rryaltiproduct continuous movement lines 132
4. Calc-ulating frrultiproduct intermittent movement lines 136
Ch. V. Controll.ing and Regulating Banks Feeding Production
Lines ("Va. P. Gerchuk, Candidate of Economic Sciences) 148
PART TWO. EXPERIENCE ORGANIZING AND OPERATING
PRODUCTION LINES
Ch. VI. State of Development of Line Production Methods in
LenIngrad Machinery and Instrument Manufacturing 171
A.G. B,~~r-man, Candidate of Economif,. Sciences, and A.I.
~Iey-markf Candl1date of Technical Sciences)
Card 5/8

Assetrpbly-lin- M~!th,-,ds 11, Serial Manufar.-turing (Cont.) SOV/1212
1. OrgarIzat'lon of prcductl-closed shops and sectors 201
2. Flow methods of work ir. preparatory shops 203
3. Single produ,,~t continuous movement lines in assembly shops 214
4. Single Droductu intermittent, movement (direct flow) lines
for machining parts 228
5. Single product intermittent movement (direct flow) lines
In assembly shops 233
6. Multiproduct continuous movement lines in assembly shops 239
7. Multiproduct intermittent movement (direct flow) lines
for assembling and mounting In assembly shops 256
8. Universal design of conveyor facilities 266
Ch. IX. Economic Justification of a Choice of Flow Variant
Based on the Example of Electric-vacuum-device
Manufact-u.ning Industry (A.P. K-.assovskiy, Candidate of
Technioal Solennc-,es) 269
Card 7/8

Assembiy-iine Methods in Serial Marrafacturing (Cont.) SOV/1212
PART TI-93E.E. FOREIGN EXPERIENCE IN ORGANIZING LINE
PRODUCTION IN SERIAL [LOT] MACHINERY AND
INSTRUMENT MANUFACTURING
Ch.. X. Basic Trends in -the Development and Experience ['Gathered]
in Organizing Line Production in Foreign Industry (A.G.
Berman, Candidate of Economic Science) 277
1. Line production problems in foreign literature. General
f e a t ur e s 277
2. Basic principles of mass and line production 281
3. Economic far;tors governing the use of line production
methods 299
4. Examples showing the organization of work flow in small
and medium size establishments 312
5. Basic trends in mechanization and automatization of
production prooesses 315
AVAILABLE: Library of Congress
JG/ksv
3-11-59
Card 8/8

IL114OV, A.N. dots., kand. tekhn. nauk; SOKOLITSYN, S-A-9dots.,kand.tekhn.nauk
I
Indices of rbZrthnical work flow and even production output in
serial machinery production. Trudy IIEI no.22:69-77 '58.
(MIRA 11:12)
1. LenjagradskAy politekhnichookiy inatitut imeni Nalinina.
(Machinery industry) (Industrial management)

SOKOLITSYN, S.A..dots.,kand.tekhn.naiilc;KLIMOV, A.N.,dots.,kand.takhn.nauk
Methods for setting up production reserves in serial production
flow. Trudy LIXI no.22:225-231 '58. (MIR& 11:12)
1. Leningradskiy politekhnicheskiy institut imeni Ulinina.
(Industrial management)

KCRBUT, A.A.; 13NICHINOV, V.S., akademik, otv.red.; NOVOZHILOV, V.V.,
red.; PINSKM, A.G., red.;_SOKCLITSYN, -S.A., red.; LUCHKINA. A.N.,
red.izd-va; SMCHMO, G.N., tekhn.red.
[Transactions of the Scientific Conference on the Use of
Mathematical Methods in Economic Research and Planning] Trudy
Nauchnogo soveshchadlia o primenenil matematicheskikh metodov
v ekonomicheakikh issledovaniiakh i planirovanii. Moskva,
Izd-vo Akad.nauk SSSR. Vol.6.[Use of mathematical methods in
technical and economic calculations] Matematicheskle matody
v tekhniko-ekonomicheskikh raschetakh. 1961. 166 p.
(MIRA 15:2)
1. Nauchnoye soveshchaniye o primenenii matematicheskikh metodov
Y ekonomicheskikh issledovauiyakh i planirovanii,' Moscow, 1960.
2. Leningradskoye otdeleniye Matematicheskogo instituta AN SSSR
(for Korbut). 3. Laningradakiy politekhnicheakiy institut (for
sokolitsy-n).
(Mathematical statistics) (Electronic calculating machines)
(Industrial management)

TATEVOSOVI, Konstantin Georgiyevich- SOKOLITSYN, S.A kand. tekbn. nauk,
1-2
dots., retsenzent; KLjl.',Ov, t;~;;;- nauk, dots., re-
tsenzent; VAPKOVETSKAYA, A.I., red. izd-va; SPEMISKAYL, O.V.,
tekhn. red.
[Establishment of norms for a uniform production flow in series-
manufacture of machinery] Normativnye raschety ravnomernogo pro-
izvodstva v seriinom mashinostroenii. Moskva., Mash iz, 1961.
246 p. ~M:IIRA 15:2)
(Mac'hinery industry-Production standards)

KLIMOV, Aleksey Nikolayevich, kand. teldm. nauk, dots.; OLENEV, Ivan Dmit-
riyevich, dots.;. e Alekseyevich, dots.f kand. tekbn.
nauk; TYAMSHANSKIY, N.D.'q kand. ekonom. na ., ots.; SHAKHIDZHANYANy
V.M., kand. tekhn. nauk; SABITOV, F.Sh.g kand. ekonom. naiik, retsena-
zent; NEYIMK, A.I., dokt.tekhnnauk, prdf-.,- -red.; GRUNKIN, M.N., kand.
ekonom.nauk, dots.,red.; RUBGRINSKIYp A.M., kand.ekonom.nauk,dots.,red.;
VARKOVETSKAYAq A.I., red. izd-va; KONTOROVICH, A.I., tekhn. red.
[Organizing and planning the operations of a machinery plant) Organi-
zatsi'ia i planirovanie mashinostroitellnogo zavoda. Moskvap Naucbno-j
tekhn. izd-vo mashinostroit. lit-ry, 1961. 512 Pe (MIRA 14:8)
1. Nachallnik planavo-ekonomicheskogo otdela Leningradskogo metal-
licheskogo zavoda imeni 9talina (for Sabito4v)
(Machinery industry-Management)

SOKOLIMYN.1 S. A. (Ioningred)
"Anwendung der Mathoden der lineezen Programierang auf
the Losung der Fragen der Verteilung und K=entraticn der Produktion neuer
Frzeugnissa."
report presented at the VII Intl. Colloq, Ilmnau inst. of Tecbnology, Ilmnau, GM
22 -26 oct 1562.

VILIDAVSKIY, Isaak Matveyevich; SQKOL1T3YR,_.a.A,, kand. tekhn.
nauk., retsenzent; KLI~UV, A.N., kand. tekhn, nauk,
retsenzent; '1AVf-21TZTSKAYA, A.I., red.izd-va; SPERANSKAYA,
O.V., tekhn. red.
[Design and operation of production lines for lot production
of machinery and instruments]Proektirovanie i ekspluatatsiia
potochnykh linii v seriinom proizvodstve mashin i pr-lborov.
?4oskva,, Mashgiz, 1962. 2-19 D. (MIRA 16:2)
(Machinery, Automatic) (Assembly-line methods)

SOKOLITSYN, S.A.
Calculating efficient uniform size for part lots. Trudy LIP
no.227:168-186 163. (KM 17:4)

SUKHANOVY V.P., inzh.;-SOKOLKIN, A.F., inz-h.
Construction of a plant for the continuous rolling of pipe.
Prom. stroi. 40 no.8g7-10 Ag 163. (WRA 16:8)
(Pipe mills)

SUKHANOVY V.P., inzh.; SOKOLKIN, A.F., inzh.
For the industrialization of erecting foundations under
rolling shop equipment. From. stroi. 41 no.11:23-26 N 163.
(MIRA 17:2)

STRELINIKOVY N.P.; BESPALOV, Ye.M.; SOKOLKIN, A.F.1 SHPINEV, V.F.; KRUPENNIKOV,
S.S.; SPEKTOR, M.D.
Some conclugions from the experiences of building a pipe rolling
mill. Prom.stroi. 42 no,11:6-9 N 164.
(MIRA 18:8)
1. Trest Uraltyazhtrubstroy (for Streltnikov,, Bespalov, Sokolkin).
2. Upravleniye kapitallnogo stroitellstva Pervourallskago
novotrubnogo zavoda (for Shpinev). 3. Uralpromstroyniiproyekt
kfor Krupennikov, Spektor).

ACC NR.- AP6036171 SOURCE CO.DE.:---UR/0209/66/000/011/0036/0042--I
AUTHOR: Gudzev, N. (Colonel', Candidate of technical sciences); Lavrik, G.
(Colonel', Doctor of military sciences); Perepelitskiy, S. (Engineer' Colonel,'
Candidatc of technical sciences); Sokolki;i, N. (Engineer; Major; Candidate of
technical sciences)
ORG: none
i TITLE: Planning operations in aviation headquarters
SOURCE: Aviatsiya i kosmonavtika, no. 1.1, 1966, 36-42
TOPIC TAGS: iob analysis, nrnani=a�~�= operations research,
PERT, economic planning, industrial management, air force organization
t'MST[4kCT: A method of preparing a functional plan of operations is described in
detail. It is said that the flow diagrams and outlines currently being prepared by
comanders 4nd officers at aviation headquarters have certain shortcomings, such as
roor estimation of the time required for each operation, lack of coordination be'-
tween sections, and no visual means for timely detection and elimination' of pot ential
I.-Ifficulties.' Many of these problems can be eliminated by adapting methods
of net-work planning and management (SPU), which are widely used in the national
economy. In this case the planned process is broken down into individual tasks.
Each task is performed in phases which are called events and are designated'
tv the resultant term, such as "aircraft fu'eled," "decision made." Consequently,
event expresses some important moment in the realization of the planned action. it
Card 1/2

AZC NR: AP6036171
Events are logically relatpd to each other by means of tasks which actually transform
one event -Lnto another. The task or operation means a working process which utilizes
time and materials; "fictional work" means either a rest period or an enforced
waiting period, which takes time but does not produce. On the basis of this terminol-
ogy, flow charts of such planning are presented and methods of computation for
determining the time allotment for each task are given. It is said that such graphic!
plans can be prepared well ahead of time n6t only for such stationary processes as
tions during alert, preparation for second flight mission, retraining of a flight
a
c
crew, etc, but also for such highly dynamic processes as the organization of
activities during training under various circumstances. Experience with this type
of planning should result in the preparation of standard plans which are periodically
revised, and in the capability for estimating work capacity and anticipating
difficulties in certain cases.
SUB CODE: 05, 12, Ol/ SUBM DATE: none

Causes of irreversibI m2etbrittlege 14 "-~jwwa
Lud V. 1). Switiliq . J
l9S5T-"In"orUer 'tekp. theclTect c4 a us,463 it
carbidic decompri. of marte"Nite, stcc!s c"Ng. C, 0-10, Cr
1.50. anti Ni 5X0; C 0.39, Si 1.12, Cr J.60, and N 5-kO;
and C 0.33, Si 1.03, Cr 3.60, and Ni 4,10% were isother-
mally quenched from 1200* at a (cuip. rnngiag from room to
slightly above the nutrten5itic~ointior5min.andifien were
~
tither water quenched or heated for 5 Inia. in the temper
brittle range, after which both sets of sptcimenswerc drawn
at *100* for I hr. The cornitu. sclected assured austenite
Qity in the 2nd hcating
range, So that only Martensite
deco entered Uic picture. The tlrvrs giv 9 Impac
s rength vs. the temp. of the first isothermic treatment shovr
-04 ~'ea
that the temper brittleness is directly connected with proc-
mes occurring in martgnsite on teruperbig it in the dangerous
interval, exprcssing itself In 'a chniactr4istic iotergrartular
-tenite
fracture along 4u3tetiltic grains. Dccojnpn.oNiu~, hLL4
noeffvcEwhatever. A utax. brittlene,~s was alivaysobserved'
when the boundariLs of austenitic gruins were filled with
m r(ensidt: crystals.
D. Gat

SOP,-
~C.:I~OV, Ye. :7
A
Ifinvestigating the irreTiersible Released Brittleness of Construction
ialoy Steels." Cand Tech Sci, Ural' Polytechnic inst, Sverdlovsk, 19.54.
(.Uhl(lim, No 21, Ilov 54)
Sur-,.re~,,,r of Sclentific and Technic~-,I Dissertations Defended at U33-L' Higher
Educational Institutims (11)
SO: S'xTI. 110. 521, 2 Jun 55

60
15164" Frvbl~nj of the Nature ef Ili. Plajt!2 Ilpformalljos
.)f Sitifurc ""i%e otSubsWrxes Svlp,;cLtcd to Frit-tion Procr-Spes.-
. . r5
CIr K v0prosix o lirfrode plastlelte-Alkh deformnivil puvnr-
~Ihfloftnykh sloey tntjh0iikhsin lot. ( % K. V. Sera-
skit. L. SoLnIkov. ruid 1'. D Sadovskii. Dokl(,d!l rikadeii
ho. 4, At.g. 1, 1955, p. (4)5-W8-
Dvn,uiiio wirl static corolim.;3imi; effixt tif tempering, tenpera-
t!,rt, iLd wigInst 'tltlCtUTP; miurnhardnesi. (,r3ph!. 3 jef

'/.91/1112 539.388 -669.15-157
-6ffeot_of Plastic Deformation (in Dokl..kk ad. 14 auk
Austenitic stilte) on Tempering 4) '6091-610 (02-
io-17 (
Brittleness of Llloy6d Structural 1955
Steal
L.V, Smirnov, E.N. SokoUov,
V.D. SadovElky LT. S. S~ R.
When combining rolling with hardening under conditiona
prcolmdIng rearystallisation of cold-hardened austenite.,
a consid-~rable repression of the development of both
reversible ar.4 irreversible tamper brittleness is observed.
Plastic deformation in austenite state follc~wed by harden-
ing (in the absence of rearysta-Uisation.) also prevents
destruction of m-,,tal along th5 botmdaries of austenite
grains. It is conceivable that plastic deformation affect,;
tM distribution and segregation of phases causing the
development of the two kinds of brittleness. The mechanisms
of the initiation of the two kinds of brittleness are,
a-ppar?ntly, Ilentical.(Blbl.5)

USSIR/Solid State Physics - Mechanical Properties of Crystals E-10
and Polycrystalline Compounds.
Abs Jour : Referat Zhur - Fizika., No 5) 1957, 11937
Author : Sokolkov, Ye.N., Sadovskiy, V.D.
Inst :
Title : Investigation of the Irreversible Temper Brittleness of
Structural Alloyed Steels.
Orig Pub : Probl. metalloved. i term. obrabotoh. Mos knia - Sverdlovsk.,
Mashgiz, 1956, 99-119
Abstract Study of the development of the irreversible temper brit-,
tleness of a large number of alloyed steels has shown that
the occurrence of temper brittleness is not connected with
the decay of the residual austenite, but is in correspon-
dence with the start and development of the carbide forma-
tion during the decay of the martensite. The irreversible
temper brittleness takes place also in the case of a spe-
cial heat treatment, vhich prevents the decay of the
Card 1/2
USEjl/Solid State Physics - Mechanical Properties of Crystals E-10
and polycrystalline Compounds-
Abs Jour Ref Zhur - Fizika, No 5, 1957, 11937
residual austenite. Carbide formation during the decay
of martensite leads., at a definite tempering stage, to a
reduction in the brittle strength upon damage along the
boundaries of the grain-
Bibliography, 34 titles,
Card 2/2

0 IV
/'P
VirraTMI d1neg"s of itiuctural ma 01BLOYS.-
a
an ru rRIF Fr.
*1-:iZ7:tQiks'b9441T1k 7~' Maw 1956. 0-
emble.temper brittleness in structural steels.
was studied as a function of (a) th tn. tetnim. of 18 steel
alloysj (b) the degree ofjd=gM~rrthe residual 11911MA11-
d
etd. majlrtetosuetrically~and expresMI by the criange la
Magnetic st ren gth Al; and (c) the degree of carbidA formation
C detd. by the 6bange in the cocreive power, air., betweon 250
and 100*. FL
metions of the impact strength o~, Ali All, mid
the hardnessffii, vs. the t~T
gering temp. I weredetti. for the
!Aowlng alloys cuatz., best es C 0,28-0.38, Mix 0.20-1.74,
i
Cr 1.27]-~1.917, P 061, and S; 0.022-0-38% the lot-
Itt
low & I N14.20%; Ci 1,77, N1
34".. 06:
3.71 43, NI 4.10,
Ni 4W.3M
SIO.22, Ni 4.3 1%; 0.11,
Co 1.09, M0.12, '4 51; My'bN CH, 0
MI. A, R. ~11 'T~' F _;/91
Cp&.61 NI 428
10. Cro: N.
N
C 11 .73, 0.40, M 8.00,
1 0
O.OWNE. M0,11
AOTC-50
oG.4 A
hN II,1NI7'W'WOB-/,,;!
W 0,32, No 1.46%. Pre
Indicated that the decomlin. of the residual'
Ite In these steels could be arrested up to a high temp.
austern
above that of the annealing pructises of martensim so that
both processig could betibservedseparately. ThavahtesoC
aj were detd. an specimens 10 X 10 X 60 min. notched after
the thermal treatment was completed- oil-quenclied from:
1100% temptredfor I hr. at the temp. rangebetween 2002ndi
'h tt
6W' in 50' Intervals, and water quenched. I emin.m e..
46 VS, I curves itt 25G-M* (defined as the Irreversible brittle-,

ness) ins present in all the steel. tested., Cr, W, and bit)
shifted the min. to higher temps., to 300-W as compared
with 25"00* of C steel; this shift was increascd by 4 and
8% Ni. No correlation was found between the curves of a&
vs. land thoscof Arva.l. Inmost specimens the decompti.
of residual austenite occurred After the min. In aA was paLied.
On the other baud, a definite relation between thiss min. And
AH. was entabli5hed; In all cases the min. ag wn-espoqdcd to
the point of carbide formation. Instech36KhX8BaadSC-
KhNSM the decrease in ah was slight; whereas AH. passed
throughawell-defintsimax, The lack of a sharp decrease in
a, was attributed to the abundance of fine crystals In these
alloys. These and earlier available data pointed to the con-
elusion that carbide formation rather ithan the decompn. of
the residual austenite (cf. Grossman.' C.A. 40, 33791) Was.
the detg. factor in the development of Irreversible tesnM
brittleness. This conclusion was further supported by stud--
les of micrograms and by the following expts.: to decrease
tti- austa-lite derompo. toa min. the effect of the duratim of,
was detl,,c,,n plects of 36KbN4C tempered at
=d,&I 16KhN I tempered at 420* for 6. 10, 20, 30,
40, and 6Q min. and ~ 1, 2 3, and 4 hn. and then water-
quenched. 'The decrease In aj with ttle duration of temper-
ing was grudual, and AU.'Increased simultancatt4y; d
compn, of residual au.5tenite was not d td in any of these
_tests.--

~RPRER Rll`;~
0 to tetiLii (i.
ett of!
ovi ti 'an
17V .4 'S.
ON
5M
No, 18, c ~vr ustbi1r,-Alloys 6f
t A] d ),0J ~0/0'~Al witre pro
Od Pon wag
-2, Out At !Ylth,0.02
s6eciwdv~R IDX 10,-X,65 w
tiesite Crucibles..:
MM em oil
2
quenched from IICXP~ tempoiia k 1.,hr. at: ti I, ro
2W to 6M* In 60' lnttfvaI5,.qiicd0_h0 Inwateri. not
-the Int a 4 ingth 44 v$, I
-for to nsile teats.' Thecurves of
of the altoy Withou to t Old 'Very"
0 low Yv 4L r
ttle: a profloutic
and a shallo, t
t
irreversible And re e; t e f =rac a
1 t the
alnc4, The a~. ".I curves Of
brittleneii range was coais~gT
0.05 and 0.16%:
the. alloys *ith At exhNtod_onIj-.
'WIS
ur -howid an increutcl amt
fine-grained amtenIte To'
dot wh0hei tffcct: cf A
t an
ducing the hTeversible brittleness, s il~e to the forma I
Wa
atlon of
of At initride, thus reventing- the form
nitrides (cf. Schm er, e el al., C-A. 44.. 4399f) or to thiJu.
drer~ont and
crease of fine-grained, structure, (cf. . Hou,
Schrader, C.A. 33, 37332) alloys contg. Q.03 aud'O.15% At I
piepd.-ht rama (0.0&-l turn. Hg). -The pxcess of At,
the absence Of N and 0.03% of Al -was not enough
to affect ak. Mi j im. I curves of both alloys wexe.prpttl-,~`
a
call Identical, pass 3'gh a sharp min. at 350* and a
L'w higx=llel'at 5M*. Ne.effect
sha er one at a -on the i
At
Co6clusion: th
grain structure was noted e effect of
-rathei
all Was due to the increc(st of the fine structure
rna Mo.
-7 to the prevention of Cr and Aln nitride for t*

Effect of VlWitic deforutittion lat thq austenitz te on a
chmeter of embrittliquient of strucittra- stems de-
vel4pad to tam -nZ,:v71r-N7'K)knIkov, and
rZA. V. SON
NZ TrU. -M ~.~Na
V. D. Saaoviff~il, 'd
No. 18, '167-41jr effect 4
ia 9
lillFc tendlucl;t Of AM to develop Irreversible
t
psto.*&,~ Fid reversible (2ad-order) brittlen".4 was-in-
vestigatO by file 101joiVing SeriCS Of tXptS. With StM3 C0111g..
besides C 0,37-4,38 and Cr 1,33-1 .63% t1to. following: 35
KWCA, Itin 1 M, 511.30, 11 OR28, S 0.t'r2)f)1r/p;. 37KI%14.lA,.,
AM 0.35, Si 0.4, Ni 3,3, P 0,018. S 0A)Itl1,';. ~ (I)After Imat-,
itig for 30 mill. at 12": the qpeehneas %vere treatedws fid"
lows-, (a) rolled at 12&) und 0-4uencheii Immediately, (b):
oven-m)led to DW*. ro)Icd..aq(j jit;mVdiaiely 6il-quenched.'
(c) oven-couled W PW* tvich-
out rolling. Tile impact'itieng-W. at of (a), (1)), and (C) of
the 2 alloys svere 1.0 and 21.3, 5.5 Q BA 0.5 unit 1..2 kgj~
111~. resp. Tile frilcture (it (U) was brittle, filtie-?kculnod.
111;1.C
in granular, characteristic of the 2nd-(irder-:brittlenc%s;i,
A that .1 ~ (1)) was ainorphou5 without it tr;ice oi brittleness;
aiii! that (if Q ivas eiiarse-grained, iutragr.,wilar., 'Cite dil-
fereace bet%YL:en (it) iktid (b) suggc-sted the pirAbility 4 in-
Slaistalleolli amienjit- recryst it, at 1200*, The~ differeue
[KAVVeett (b)'111d (e) CIIII)II.-Wited (fit, CiTeCt of 114't fichirulation
brittUntess, ~ (2 ' Nkf' tiVert
1) Specimens lield (,,r I lit. at - I
oven-m&A to fitH)' and U) with-
Out rollitig aild (111 Imt-Wilvd i-villictimi and thell oil- 0
quenellett. llivcvs of L-Aith groulis wt-re Ilies, testillerLd far I
fir. in a salt bath at 50' iottryals in the range of -w Woo
The Itarduess its it function of tht! tettilieritig tcjfl~j . ;. %Vcre~
The ctirve
para -Ilrvt~ (kcrea',ing sliglitly It,; I ill"re.tivil.
if a, vs. I tit (a) pa.,ied thraittgl;u min. :it :i max. as
450', and.anotfler mill.at The carves of Itivevs
.0

It
p~d it udthcn,r*i;e;&nta1;!ly.1
n
= /9
KbN3JA
varla m Mth 37
h
h
i
t
t
an W
j~FGCA The e t of gree of rolling i

on 4' w" e
oc.-c.1,d from 1150- t. OMO
*n Vece-1

,,,.
rolled b -quenched it
110, and 30% reduction, and oil
mediattlY. The max. rise of aA, was completed at thL lowest
101/a, reduction. Further rolling had no effect oyl a4; in
some cam It was slightly decreawd. Thiswasanindication
that the effect of hot-rolling was not due to the fibrous grain
an d fracture. for practh-al I y al I of V te clo a ga t ion, and fi b ro its-
new,,wasmmpletedatlO%reductioti. (4) ailts a function of
the temp. of hot-rolling Increased Iiijearly with the temp.,
passed through a rounded max. at MHO00% and then de-

creased linearly. :These expts.
were made %Wlb allo
Y__

___,ULU5ntg. C 0.34, Mn OX, Si OM, Cr 3.23, and Ni 4,84.",,
The other alloys gave similar results. (5) The erject of ilia
time h-14 at the rolling to-nip., after rolling before wattl
and rolled
quenchj,',C was det4. on pieces preheated at 1200'
at 1200,%'100, 10M. 9W, and 800* and held at these temps.
for 1, 5, ai~i 20 mbi.-. The function ai vs. the time held at thel

-A I rolling terk%-. decreased ex`pclncnWlly,-.and this~effect inJ
t of hot-rollini
Vkh'the rolling temp., ...1hiis1he effee

c
M le t Liu, fK
rn-.Y4 Ic 11
bA
td -Mkkn - ins,
tii of W
N

t
n 'i
Jndlcited-tluivat 120' ts
tumd keg n
p
'tu'l, Y I
instantaneous and that IV A Pp y
tically

L
V DLn
EM SA*8K
V
V
1)
'
,,
.
j
,
I
I
~nchL -S.
0
mg. 1 (0) The variatma of ai, as a function of the test-,
q
1.
9 temp. -bras detd. Itt the range of +140 to ---200*, aA bt-
gan to decrease into the brittlenc.1% range at W when )IM
rolted "d at +100* when not rolled, Conclusion: Ifotj
mcch.working reduced both revasibleand lumnibte tcnl
per brittleness providing tecrystn. of amitenite was in
'arrested. Both types of brittleness are si~niUt r prix-esses but!
Initiated by different causes.

SOV/ 137-38-9- 19827
Translation from: Referativnyy zhurnal,lvletallurgiya, 1958, Nr 9, p 246 (USSIR)
AU T HO P-,S: Sadovskiy, V.D., Malyshev, K.A., So.kP1,1&Q_Y__Y_q,,N., Smirnov,
L.V., Bogacheva, G.N., Biryulin, V.T., Petrova, S.N.
U IT L, E: 'rhe Effect of High-temperature Plastic Deformations on
Brittleness of Hardened Steels During Tempering and Aging
(Vliyaniye plasticheskoy deformatsii pri vysokikh tempera-
turakh na khrupkost' pri otpuske i starenii zakalennykh staley)
PERIODICAL: V sb.: Issled. po zharoprochn. splavam. Vol 2. Moscow, AN
SSSR, 1957, pp 76-91
ABSTRAC T: Investigations were performed in order to determine the
effect of thermornechanical Zreatment (TMT) procedures (plas-
tic deformation in the austertite state combined with immediate
quenching of austenite which had not been allowed to recrystal-
lize) on the ak of steels 35KhGSA and 60Kh4G8N8V, and on the
ak of special grades of heat-resistant steels. Mechanical prop-
erties of the metals involved were measured and metallographic
investigations were performed. The TMT increases the ak
value of austenite steels which are susceptible to aging (thermal
Card 1/2 brittleness). The lower limit of the temperature of TMT

SOV/ 137-58-9- 19827
The Effect of High-temperature Plastic Deformations on Brittleness (cont.)
corresponds approximately to the position of the austenite recrystallization
temperature for a given alloy. Since the value of the maximum temperature
for the TIVIT is dependent on the tendency of austenite toward growth of re-
crystallized grains, the conditions of the TMT must be such as to preclude
recrystallization of austenite. The effects observed are attributable to the
fact that the deformation becomes progressively localized on grain bound-
aries as the temperature is increased and the coefficient of work hardening
is diminished. This localization of the deformation, in turn, leads to
changes in the form and the distribution of precipitated particles formed in
the process of tempering and aging and, owing to the fact that the ak of the
steel is determined by the nature of the precipitated particles, results in a
reduction of temper brittleness.
L. M.
1. Steel--Deformation 2. Steel--Temperature factors 3. Steel--Heat treatment
4. Steel--A.ging
Card 2/2

kandidat tekhnicheskikh nauk.;SMIENOV, I.V., kandidat
tekhnicheskikh nauk.
Effect of heat treatment and mechanical working on the temper
brittleness Of strUctural alloyed stools. Metalloved. i obr. mt.
no-3:31-35 Mr 157. (NLRA 10:4)
1. Institut f iziki metallov Urallskogo f iliala Akademit na-ak SSSH-
(Steel, Structural-Metallography) (Steel-Brittleness)

AUTHOR: Sokolkov,-E.N. and Sadovskiy, V.D. 130
TITIB: Influence of plastic deformation by tension on the notch
impact strength of alloy structural steel in the case of
exclusion of processes of recrystallisation of austeni-Ve.
(Vliyanie goryachey plasticheskoy deformatsii rastyazheniem
pri isklyuchenii protsessov rekris-U"allizatsii austenita
na udarnuyu vyazkost' konstrukstionnoy legirovannoy stali.)
PE RIODICAL: "Fizika Metallov i Metallovedenie", (Physics of Metals and
11.letallur~y~q Vol.IV, No.1 (10)
p.187, (U.S.S.R.)
57? ,
,
ABSTRACT: The autho-T-s carried out tests of hardening during deform-
ation in tension of a steel of the folloviing

', i
0-80-1-10 r
.390/,', C
composition: 0.32-0 1 S I/ ~ e,
1-10-1-40
-
,
2
1.10-1.40c,,o'~ Cr, 0.110,1'~ lLax Nti. A decrease was observed in the
development of reversible temper brittleness which is accom-
panied by an increase in the impact strenrth and a changeover
to tough ductile fracture without any visible traces of brittle
intuer-crystalline fracture. -The defomat-ion in-tension of the
specimen in the austenitic state was effected a*m a .special--
attachment to an hydraulic press. For excluding re-crysta
satuion of,the austenitue an increased deformation rate of
~) =/sec was ap~jlie-d with ra-.)id hardenLnE; after completion of
the stretchi-n-n-. 3 Russian re~fer~ences.
Institute of L,etual Physics, Ilecd . 'NoVeLTCbr_-r, 2, 1956.
Ural Branch of the Ac.Sc.

SOV/126-6-2-12/34
AUTHORS: Sokolkov, Ye. N., Smirnov, L. V. and Pet-rova, S. N,
TITLEI: Influence of Thermo-mechanical Treatment Unde_- Conditions
of Forging on the Impact Strength of Alloy Steels
(Vliyaniye termomekhanicheskoy obrabotki v usloviyakh
kovki na udarnuyu vyazkost' konstruktsionnykh
legirovannykh staley)
PERIODICAL: Fizika Metallov i Metallovedeniye, 1958, Vol 61 Nr 29
pp 276-280 (USSR)
ABSTRACT: In earlier work (Refs.1-3) it was established that
combination of hot rolling of steel in the austenitic stat,-,
with a bacdenuffig --regime skA as to elidnate recrystallisation of
austenite enables to reduce the drop in impact stren6th
after tempering at temperatures at which temper
brittleness develops. The authors considered it of
interest to study the effect of such "thermo-mechannical"
treatment under conditions of free forging. The experi-
ments were effected on the commercial steels 37KhNZA and
35KhGSA. As blanksl be&ss of 20 x 20 x 200 mm were used;
the forging was effected by means of a pneumatic hammer
C:> -
with a reduction of 20%. Fogr differing regimes weSe
Card 1/4 used, namely: heating to 1150 C, coolinS down to 950 C1

SOV/126-6-2-12/ -311
Influence of Thermo-mechanical-Treatment under Conditions of
ForEing or, the Impact Strength of Alloy Steels
forging, quenching; heating to 1150 0C, forr-in~,,, quenchin-;
U b
heating to 11500 C, cooling to 0,50"'C, forging, soakinS in
a fu3nace (1150 C for 5 minutes), quencginE; heating to
1150 C, quenching. The cooling to 950 C was a3)Dlied as
a means of impeding possible recrystallisation au-ring
forgi ng. For the same reason the time necessary for
obtaining -the desired reduction was reduced to the
possible minimum and amounted to 4-5 sees which was:
.Lollowed immediately by quenching. After quenchin6,
standard specimens of 10 x 10 x 60 mm -wiere pro-,uced by
grinding for impact bend tests. All the speci.faens 1.~,rere
tempered at a teinperatuSe at vi-hich reversiole te_-,rper
brittleness occurs (550 C for four hours). On the
finally machined specimens a notch 2 mm wide, 2 mul deep
with a curvature radius of 1 mm at the bottoa of tHe
notch was produced. The obtained imDact stren--l-
,.h aiad
r. ~T --
hardness values are given in a table, p 276. i:i~Lcro_
structure photographs and photographs of fra-ctures are
reproduced. It was found that
Card 2/4 treatment under conditions of forgin6 as well aS -Lul-der

SOV/126-6-2-12/34
Influence of Thermo-mechanical Treatment Under Conditions of
Forging on the Impact Strength of Alloy Steels
conditions of rolling brings about a reduction of the
sensitivity of the steel to develop reversible temper
brittleness. In both cases this effect is associated
with the localisation of the deformation along the
boundaries of the austenite grains of t'~Le initial heatinS,
distortions in the crystal la-4-t1ce of the intergranular
transient zones (which are coifserrved after hardening)
and the thereby caused change in the form of -the phases
and compounds which are responsible for developinS
temper brittleness. The here described effect of
thermo-mechanical treatment can also be obser--ed in other
types of bat working as, for instance, stamping -and extrusion,
under conditions such that recrystallisation of work-
hardened austenite is prevented.
Card 3/4

SOV/126-6-2-12/34
Influence of Thermo-mechanical Treatment Under Conditions of
For.'--,ing on the Impact Strength of Alloy Steels
There are 3 figures, 1 table and 4 references, 3 of
villich are Soviet, 1 German.
ASSOCIATIO'Li: Institut fiziki iaetallov Ural'skogo filiala AN SSSR
(Institute of Metal Physics, Ural Branch of -the
Ac.Sc. USSR)
SUBMITTED: November 19, 1956.
Card 4/4 1. Steel-Mechanical properties 2. Steel--Temperature factors
3. Steel--Test results

SOV/1-26-6-4-30/34
AUTHORS: Sokolkov, Ye, N. and Petroval S. N.
TITLE: 0 he Mechanism of the Effect cf Plastic Deformation
itRustenitic State on the Temper Brittleness
(0 mekhanizme deystviya plasticheskoy deforraatsii
v austenitnom sostoyanii na otpuslmuyu khrupkost')
PERIODICAL: Fizika Metallov i Metallovedeniye, 1958, Vol 6, Nr 4,
PP 762-764 (USSR)
ABSTRACT: Transition to brittle fractlure (cold brittleness
temperature) is closely associat-ed with the ratio of the
yield point to the brittle strength of the material.
Steynburg and Popov (Ref 5) found that for the case of
temper brittleness a high temperature of transition to
brittle fracture is the result of a reduced magnitude
of the brittle strength. The authors of this papar
considered it of interest to establish the reasons for a
decrease in the temperature of transition to brittle
fracture of steel in the state of temper brittleness
caused by thermo-mecha-nical treatment, it was assumed
that the observed decrease in the temperature of
Card 1/4 transition to brittle fracture is due to an increase of

SOV/126-."5, "-_N~/3'4
On the Mechanism of the Effect of Plastic Defoiiiation in the
Austenitic State on the Temper Brittleness
the brittle strength, This seemed likely since therr-o-
mechanical treatment leads to a suDpression of the
brittle fracture alonG the boundaries of the austenitic
grain which is characteristic for temper brittleneas,,
whilst a weakeninE of the grain boundaries during the
evolution of phenomena causing temper brittleness brings
about a reduction in the 'brittle strength, To verify
this assumption, the brittle stren-th was detel-Mined
for epecimens of steel 20KhNZ after aardening from
1250 C, preliminary tempering at 650 8C, followed by
rapid cooling and subsequent tempering at 55-0 G for
4 hours; the impact strenSth waG 1.5 kgm/cm2 with a
sharply pronounced brittle intercrystallite fracture,
To enable easier observation. 'of the development of the
brittleness and also for obtaining a grain size as
large as practicable, the appiied 'riardenfng temperature
was higher than usual, The thermo mechanllcal treatment
consisted of deformation by rolling on a laboratory
hand-driven stand with a reduction of 23% at P, speed of
Card 2/4 5.7 m/min. The heatJ*ILntL temperauure.was 1250"C, ho~,.,ever,

SO V/12rc- 6-4. -340,1314
On the Mechanism of the Effect of Plastic Deformation in the
Austenitic State on the Temper Brittleness
the deformation was effected at 900 OC so as to suppress
recrystallisation of the work-hardened austenite.
Hardening of the deformed specimens was effected
immediately after rollin6 so that the time interval
Iroin the ending of the rolling to the instant of
hardening was 0.1 to 0.2 see. From the rolled material,
small specimens of a diameter of 3.5 mm. and non-standard
impact specimens of 8~5 x 8,5 x 55 mm were produced,
Similar sDecimens were alSO Droduced. dnd hardened in the
normal way. The imDact and the tensile specimens were
manufactured aftsr the final heat treatment, namely,
tempering at 550 C for 4 hours, On the basis of the
obtained results it is concluded that the reduction in
the temper brittleness observed in the case of coalbinin~~,'
plastic deformation in the austenitic state with
Card 3/4 hardening under conditions excludinp- recrystallisation
0

OV/1 2 0/
'~;n the i~iechanism of the il~ffect Plastic 1'jefrr.,,.,a'L-'-io,-1 in
Austenitic State on the Temper Bri-uftleness
of the work hardened austen-ite is due to an increase
in the brittle stren,-;th,
-There are '31 Soviet references,
ASSOCIATIO11: InstiWt fiziki metallov Urallskogo filiala AN SSSR
(Institute of Lietal Physics, Ural Branch of the
Ac.Sc. USSR)
SUEMITTED: December 7, 1957
~Jard 4/4

AUTHORS: Sadovskiy, V.
TITLE: Appearance of
Solid Solution
khrupkost' ri
asnove medi
SOV/126-6-5-41/43
D.,and,,Sokolkoy,._je. N.__
Brittleness in the Decomposition of a
of Mn and Si Based on Copper (Yavleniye
ra pade tverdogo rastvora Mn i Si na
PERIODICAL: Fizika Metallov i Metallovedeniye, 1958, Vol 6, Nr 5,
Pp 954-955 (USSR)
ABSTRACT: The process of decomposition of7copper based solid
solution with 1.5% Mn and 3-5~6 Si (manganese-silicon
bronze) and its relationship with plastic properties were
studied. In the decomposition of this solid solution
a second phase separates out (Refs 1,2). This second
phase is Mn2Si and it is assumed that it does not affect
the plastic properties of the bronze (Ref 3). The
present paper deals with further studies of this process
and its effect gn plastic properties. The bronze was
hardened at 8OOuC. Such a treatment ensures complete
dissolution of Mn Si and subsequent rapid cooling on
quenching producei a saturated solid solution at room
Cardl/4 temperature. A series of samples subjected to the above

SOV/126-6-5-*1/43
Appearance of Brittleness in the Decomposition of a Solid
Solution of Mn and Si Based on Copper
treatment wgs tempered at temperatures of 200-7500C in
steps of 50 C. The duration of tempering was three hours
and the samples were subsequently quenched in water.
Microstructure studies of the samples showed that in the
hardened state the alloy is homogeneous and it consists
of uniform grains of the a-phase (Fig 1). As the
temperature of the subsequent tempering is increased, the
sec8nd phase separates out in the alloy starting from
350 C tempering. The amount of Un Si s8parating out is
greatest in samples tempered at 506-600 C (Fig 2).
Impact -tests were carried out on samples of 10 x 10 x 60 mm
dimensions with notches 2 mm wide and 2 mm deep. The
results showed no dependence of the impact ztrength on
the degree of decomposition of the alloy. A second series
of samples, which had undergone the treatment described
above (hardening and tempering), were further subjected
to cold plastic deformation by rolling at the rate of
1.5 m/min. The reduction in size during rolling was 30%.
The initial size of the samples was chosen to make the
Card2/4 final dimensions the same as for the first series, i.e.

SOV/126-6-5-41/43
Appearance of Brittleness in the Decomposition of a Solid
Solution of Mn and Si Based on Copper
10 x 10 x 60 mm. Fig-3 shows the results of tests of
samples subjected to cold plastic deformation. The
ordinate represents impact strength and the abscissa
represents the tempering temperature. This time the
plastic properties are obviously affected by the decomposi-
tion of the alloy and the minimum of impact -strength
occurs at those tempering temperatures (500-6OOuC) which
produced the largest amounts of the second phase ~n the
alloy. Impact -strength decreases from 19 kg.m/cm for 0
cold-rolled sajAples which were previously tempered at 250 C
to ~5 kg.m/em-' for cold-rolled samples tempered at about
600 0. These results are in agree with the data obtained
from the microstructure. The observed behaviour is due to
lowering of the degree of plasticity of the alloy by
previous plastic deformation; such a lowering of
plasticity makes it possible for the second phase (Mn 2S')
to produce the expected embrittlement of the alloy.
Plastic deformation of a 2-phase alloy produces also high
internal stresses which are higher than the stresses in
Card3/4 the corresponding alloy consisting of a single phase.

SOV/126-6-5-41/43
Appearance of Brittleness in the Decomposition of a Solid
Solution of Mn and Si Based on Copper
There are 3 figures and 3 references, 2 of which are
Soviet, 1 English.
ASSOCIATION: Institut fiziki metallov Urallskdgo filiala AN SSSR
(Institute of Metal Physics, Ural Branch of the Ac.Sc.,
USSR) 5
SUBMITTED: November 5, 1967
Card 4/4

A&THORS :-Sakalk~ ~,N., Candidate
Lozinskiy, M. G., Doctor of
Antipova, Ye. I., Engineer
TITLE: Structure of Grain Boundaries
Austenitic Steel (Struktura
austenitnoy stali)
SOV/129-58-11-3/13
of Technical Sciencev,
Technical Sciencesand
and Heat Resistance of
granits zeren i zharoprochnost'
PERIODICAL: Metallovedeniye i Obrabotka Metallov, 1958, Nr 11,
pp 19-25 + 4 plates (USSR)
ABSTRACT: Hardening of the boundaries of austenitic grains,
detected during impact bending tests and also as a
result of static tensile stresses at liquid nitrogen
temperature (Ref 6), leads to the assumption that the h~da-iing
is accompanied by an increase in the resistance to plastic
deformation at elevated temperatures. Therefore, it was
considered advisable to investigate the influence of the
structure of the grain boundaries in the austenitic steel
60Kh4G8N8X on the creep speed. After hardening from
1100-1150 C9 this steel has an austenitic structure and
possesses a high impact 0strength, 30-40 kgm./cm. . Ageing
in the range of 600-800 C results in separating out of
Card 1/5 a carbide phase which brings about a drop in the impact

SOV/129-58-11-3/13
Structure of Grain Boundaries and Beat Resistance of Austenitic
Steel strength to 3-5 kgm//cm 2. The deve ent of brittleness
is accompanied by inter-crystallitifffisruptions. 0 It was
established that rolling of steel at 900 to 1000 C under
conditions excluding recrystallisation of austenite leads
to a reduction in the brittleness. The authors considered
it of interest to compare the established influence of
plastic deformation on the impact stren~;th with the creep
speed at elevated temperatures. The experiments were
effected by means of the test device IMASh-5M which permits
studying the micro-structure during heating and tensile
tests in vacuum (Refs.?-9). The material was prepared for
the investigations as follows: the blanks were heated to
1200 C and0allowed to cool to the rolling temperature
(1000-1100 C). Rolling with a reduction of 25% was
effected on a laboratory rolling stand. For preventing
recrystallisation of the work hardened austenite, the metal
was cooled immediately afterwards in water, whereby the
time interval between the end of the rolling and the cooling
process amounted to no more than 0.2-0.3 see. A part of
the blanks which were n8t subjected to deformation were also
Card 2/5 hardened from 1000-1100 C. Following that, the blanks were

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel
aged for a duration of four hours at 750 OC and then
specimens were cut out to a shape as shown in Fig.l. The
flat surface of the specimen was ground and chemically
etched for the purpose of revealing the structure. The
etched strusture was conserved during subsequent heating
to 900-1000 C in vacuum and this enabled observations of
the changes in the structure during plastic deformation.
For measuring the deformation during the tests a number
of indentations were made on the ground surface; these
were arranged perpendicular to the axis of the specimen
with spacings of 6 mm; during the tests the distance
between the individual indentations were measured with an
accuracy of + 11L. The specimen was heated by passing
current direitly through it, whereby the temperature was
controlled by a thermocouple which was welded onto the
specimen. All the changes in the structure observed
during the tests were recorded by photographing one and
the same spot of the ground surface. The micro-structures
of the specimens after three heat treatment regimes are
reproduced in Fig.2, wheEeby the duration of ageing in all
Card 3/5cases was 4 hours at 750 C. The test results graphed in

soV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel Fig.3, i.e. the changes in -he elongation of the steel
U
60Kh4G8N8V with various initial structures as a function
of the est duration at 900 C and an initial load of
5 kg/mm. , show that the behaviour of the specimens differs
greatly for differing initial structures. It can be seen
from Figs.4 and 5 that in ordinary speciWens,as well as in
spocimeni; prellmixiat-ily deformod tit 1000 C,cracks will
appear and develop along tho boundarlos of bhe austonible
grains. The influence of partial recrystallisation at
elevated temperatures on the heat resistance is graphed in
Fig.3; a special experiment (curve 4) shows to what extent
the creep speed can increase when crystallisation develops.
On the basis of the obtaiDod results the following
conclusions are arrived at: For the investigated alloy
an increase in the heat resistance will be brought about by
such changes of the structural state of the austenitic
grain boundaries which result in an intensive distortion
of the preliminary plastic deformation under conditions
excluding development of recrystallisation; a decrease in
Card 4/5 the creep speed is linked with braking of the plastic

SOV/129-58-11-3/13
Structure of Grain Boundaries and Heat Resistance of Austenitic
Steel
deformation along the boundaries of the austenitic grain;
hardening of the alloy is apparently also determined by a
change in the fine structure throughout the entire body
of the grain.
There are 5 figures and 9 references, 8 of which are
Soviet$ 1 Czech.
ASSOCIATIONS: Institut fiziki metallov UFAN SSSR (Institute of
Metal Physics, Ural Branch of the Ac.Sc., USSR) and
Institut mashinovedeniya AN SSSR (Institute of Mechanical
Engineering, Ac.Sc., USSR)
1. Steel--Structural analysis 2. Grains (Metallurgy)--BoundaryI 1~yer
3. Grains (Metallurgy)--Crystal structure 4. Austenite--Metallurgical
effects
Card 5/5

3/123/59/000/008/001/043
AOO4/AOO2
Translation from: Referativnyy zhurnal, Mashinostroyeniye, 1959, No. 8, p. 12,
28674
AUTHORS: 'Shteynberg, M. M., Sokolkov, Ye. N., Varaksina, M. N.
TITLE:
PERIODICAL: Tr. Ural'skogo politekhn. in-ta, 1958, Vol. 68, PP. 54-58
TEXT: Plastic deformation which is effected by monoaxial static tension
leads to a considerable increase in breaking strength, whi.3h was determined
during tensile tests at the temperature of liquid nitrogen. The intensity of
such an increase depends on the alloy composition and the Initial structure.
Systematic data on the dependence of breaking strength on preliminary plastic
deformation may be used for a more founded estimation of the tendency of alloys
to brittle failure. Besides, such data make it possible, in a number of cases,
to determine the breaking strength of some steels by the extrapolation method.
B. A. M.
Translator's note: This is the full translation of the original Russian abstract.
On the Problem of the Tendency of Metals to Brittle Failure
Card 1/1

4.j
art.
&q
1 0 9 "
v. r,
a v 3
R.1
ARIs
MIN
2-u -a
Va V - Z~!. -
3
F
o S-8 av
3I V
.6
AR 5
doo , ;, 1.a I ~
AV. a

9 1
lie k k
Ali A
H
a ;-, - -~

A .
X q1
. A ~
o
.E
SI
s
to

AA

.

ig
A * 9
I

1~i 9 8
'as

A
o
1
~
4

S/137/60/000/009/015./029
A006/A001
Translation from; ReferativnTj zhurnal, Metaliurgtya, 1960, No. 9, p, 250,
# 21524
A MHORS Sokolov, Ye.N., Sadoirskly, V.D., S.N.
TITLE; Structure of Austeni,.ic X~~rain Rounrdariel% d Temper Brittleness of
s
Structural Steels
PERIODICAL, V sb.: Nekotoryye probl, prcchnosti tverdo&~ tela, Mosc-zw-Lentr-
grad, AN SSSR, 1959, PP. 165-171
TM. - The authors investlgased 'th= mechanism of t'-he effect of heat and
mechanical trea~Tent on the weakenijIg of 4:nmper br-ttleqess of S'ruc-,~ural a!Icy
nNz))'v-_xrCA (35KrGSA))7'*35Xj44[O (35KhN4Yu)~band 3OXH8 (30KI-MS
2OXH3 (2oK 3-1~ C
steel's. it is established that the weakening of the temper brittleness of snrii.-
n
tural alloyed steels during the thermomechanical Treatmenll is connected wit
higher values of brittle stl'xength. Plastic defc--m-ation in austlenltf:~ state -xnder
conditions preventing the development of recryz-.alliza'~-,:in of hardfaced austenite
Card 1/2

S/l 3-T/60/000/009/0 nz~c 2;-~
A006,/AO0 I
Structure of Austenitic Grain Boundar'es a-,,d Temper Bri~tjenev-- of Str i al S
UC t I r t e ej-:~
causes distortions of the gra4-n b----indlarlez, The c~.mblnp--,- -,~-f zuch
a -,treatment with quenching for Structural alloyed sLeels weakens I.ht reve--S'-t--l-
temper-brittlen%ess. Mere are 9 referc-n~.es,
K.M.
-rslatcrls note-, T'his is the full ~ransla-ti---n :~f T-e -riginal Rus-cziar a
ra S "T
Card 2/22

130) 7 18(7), 2L~(6) SOV/126-?-2-31/39
AUTHORS: Sokolkov, Ye. N. and Petrova, S. Y1.
TIITL,t~: Influence of-Plistic Deformation of Steel 35KhGSA in
-the Austenitic State on the Bature of Fracture in the
Temper Brittle Condition (Vliyaniye plasticheskoy
deforinatsii v austenitnom sostoyanii na kharakter
razrusheniya stali 35KhGSA v sostoyanii otpusknoy
khrupkosti)
PERIODICAL: Fizika Diletallov i Yietallovedeniye, 1959, Vol 7, Nr 2,
pp 306-308 (USSR)
ABSTRACT: Plastic deformation of metals in the austenitic state,
combined with quenching under conditions which exclude
recrystallization of the worked austenite, lead to a
decrease in the development of temper brittleness
-he transition
(Refs 1 12). In this case a lowering of t
temperature of brittle fracture, as well as suppression
of a characteristic temDer brittleness fracture along
the boundaries of the austenitic grains that existed
prior to quenching of the steel (Ref can be observed.
In series experiments, steel fractures,, in the case of
brittle fracture, after therao-mechanical -t-reatnent,'
Card 1/6 occur not along the austenitic grain bo-andaries as after
C~

SOV/126-'7-2-3,1/39
Influence of Plastic Deformation of Steel 35ErGSA in the
4 n
Austenitic State on the iiature of Fracture -L the Temper Brittle
Condition
normal quenchinG, but across the grain bodies. Brittle
fracture along the austenite grain boundaries does not
OCCUE even when the testing temperature is lowered to
-195 C (Ref 3). The conclusions arrived at as to the
nature of fracture are based on a microscope study of
the appearance of the fracture at a magnification of X5.
These conclusions are in a certain measure subjective,
and hence special investi-ations were necessary. To
this end a study was carried out in which the nature of
the failure of steel 35KhGSA in the brittle state, after
normal quenching and after thermo-mechanical treatment,
was investigated by a Imown method,, involvin.,- destruction
of the specimen at a sufficiently low temDerature, and
compared with a previously prepared and etched
microsection (Ref 4). In order best to be able to
observe the characteristics of brittle fracture, the
steel was heated to a temperature of 2500C prior to
quenching. Plastic deformation in the procBss of thermo-
Card 2/6 mechanical treatment was carried out at 900 C (on

SOV/126-7-2-31/39
ififluence of Plastic Deformation of Steel 35.KhGSA in the
Austenitic State on the Nature of Fracture in the Temper Brittle
Condition
cooling from 1250 OC); it was necessary for the deformation
temperature to be lowered in order to facilitate
supression of recrystallization of the worked austenite,
as exclusion of recrystallization is the main condition
for carrying out a thermomechanical treatment.
Deformation was carried out by rolling in a laboratory
hand-roller, in which a cross-section of 10 x 10 mm was
reduced to one of 8.5 x 8.5 mml i.e. by 28%. The rolling
speed was 5.7 m/min. ContEol specimens were qugnehed
also after heating to 1250 C and cooling to 900 C. oThe
control and deformed specimens were temDered at 550 C
for 4 hours. A section was prepared on one of the faces
cf the specimen, perpendicular to the axis of out, and
etched in a solution of picric acid in xylol in order to
expose the austenite grains. in Fig 1 a photuograph of
the structure in the region of probable crack propagation
of a specimen having under--one thermomechanical treatment
is shown. In Fig 2 a photo2,raph of the same place of the
Card 3/6 section is shown after the specimen had fractured at a

60V/126-7-2-31/39
influence of Plastic Defor2ation of S"teel 'USA in the
Austenitic S ate o ac ure ir the Tem-er Erittle
i the Nature of Fr U
Condition
temperature of -1950C. Whereas failure of a speciialen,
having under6one normal quenchin--, tak-es place alon-,~ the
boundaries of austenite grainis, %,hich form on lieatinS
the steel prior to quenching (S". F. Yurlyev and
Z. P. Xusnitsina (Ref 4) have this convincin,-1,,i
C)
by means of the 0method under consideration), a specimen
at 0
de f ormed ~00 C and quenched lander conditions '.-hich
exclude recrystallization of the worked austenibe, fails
in such a way -that the fracture crac~_k does not coincide
anywhere with the austenite -;rain bo-,andaries, i.e. failure
occurs across the ,rai-n bodies (Za,3~ -Figis 1 and 2).
In Fi-; 1 the line of demarcati-on reDrodu3ing the
boundaries of failure in accordlknce~ with Fig 2 is marked
bv dashes. Thus, it can be ~ssuumed that ivhen -,)lastic
d~_formation in the austenitic 's'tatle is carried out
-together with quenching under conditions of reversible
tefaDer brittleness develo-oment, the characteristic temper
Card 4/6 britlltleness~ along the austenitic ~__-rain boundaries will be
suppressed. It is impossibl6 to 1-nore the relationshi~o
Z~D -

SOV/126-7-2-3i/39
influence of Plastic Deformation --f Steel 55K!--,GSA in the Aus-41enitic
-1 , - ` 4U I 'U J_ 0 n
ouate on the Nature of Fracture in, -0"',e Gond~' '
bet-,.,ieen this fact an.:.i Llrjose ~~ ziaL~es ii~ s.r'ructure -,;IJ'-iich
arise when the above treatment if~ '_:,._Dlied.
These changes consist, as a Inule, in a strong distortion
of the shape of the austeni-'U-~! Grains - a pronouzced.
serration, the period of whic.h is many times smaller than
the cross-sectional dimension of the grain (10-201i,Fig 3).
In sorae cases, however, no such serration is observed.
Special e.xperiments have sho-~---_,a that this depends on the
temperature Of T)laSU'_JC 'Ne shali not deal
with this problem specifica'!_~_.-, ~-2-at n,3'u-e that a loc~-,I-
isation of defornation alorq-,, austenite ~-r~j
boundaries, which can be obs,:-.veJ deforLaa-11-il-In -th-1-ouoh-
out a fairly wide temperature is mos-u favourable
from the Doint of view oi' Ghei~:aou,:~chanical treatment
effect when serration oc3-%;.r~ . 1t '-has ~:,_'Lready beef
assumed that a localisati3-n ~,'L v;la~_tic, in
the austenitic grain bovur-darie-3 to chan-es in the
intergranular transition zzoi_3o Z'Ulci i:e-ions ad-joininG them,
which can alter the and ~~he mnq-nTler Of precipi-
tation of such phases vihic-_- cause de'velopment of brittle-
Card 5/6 ness (Ref 1). In fact) as now can be seen, the visible

16oV/126-'I -2-31/59
-ht~ ~.usteritic
iation of _~51'--_~SA int
Influence of Plastic Deforr , I -
State on the Eature of Fracture in the --_--'e-a;~er Brittle; Con'-Lition
distortions of the austenitic -rain boundaries (Fi-- 3)
cannot leave unaltered the nature of T)reCiDitation of any
components responsible for the develop-taent of tei~per
brittleness. The formation of e--ibrittling coliipwients of a
film-, plate-1 or net-like appearance is excluded. -which
prevents the propagation of a brittle fracture crack along
-the austenitic grain boundaries after normal q._U,;nchi__a6.
It should not be assumed, holaever, that a suppression of
failure along the austenitic ~;rain boundaries e_rr~-irelv
excludes develo-oment of temper brittleness. Special
exper4ments have shown tuhat. ste-=1 It
navin-
4
alt_laouE~h
thermomechanical treatmcnt, Se_*j I
only to a very slight e:r_te-n,. !-.j coolinL-,- _-oate after iaigh-
U
-temperature teaperi%. This ser-,j-e as t!_- ba-sis of a
conclusion which is importaiib- La the theory of zeL:-per
brittleness: processes causin:-- the development of temper
brittleness essentially along the austenitic grain
boundaries, also take place throughout the grain bodies,
but their intensity is insiSnificant. There are 3 figures
Card 6/6 and 4 Soviet references.
(Note: This is a complete translation except for FiG.caps)
ASSOCIATIOET: Institut fiziki metallov AN SSSR (Institute of Metal
Physics Ac Sc USSR)
SURAITTED: Decembel 2l;__1W?

7,570 0 6 7 71-6
P.2 0 0
AUTHOR: Sokolkov, Ye. N. )cZ`)0V/l26--?-.~_12/44
~u
TITLE: Influence of Plastic Deformation in the Austenitic Statei
on the Kinetics of thq Development of Temper Brittleness
of the Steel 30KhGSAII(Vliyaniye plasticheskoy deformataii
v austenitnom--s-U-M-yanii na kinetiku razvitiya otpusknoy
khrupkosti stali 30KhGSA)
PERIODICALa Fizika metallov i metallovedeniye, Vol 7, Nr 3, pp 384-
368 (USSR) / C1,6-7
ABSTRACT: Plastic deformation in the austenitic state leads to a
considerable decrease in the development of temper brittle-
ness in structural alloy steels if the worked austenite is
not allowed to recrystallize (Refs.1-3). It has been
assumed that one of the reasons of the suppression of temper
brittleness development is a possible change in the kinetics
of the precipitation of phases causing the brittleness (Ref.1).
The authors h&ve made a study of the influence of lengthy
soaking during tempering on the development of brittleness
in the steel 3OKhGSA. The steel was heat-treated by
Card 11L~ normal quenching and tempering, as well as by a method in

67716
BOV/126-7-3-12/44
Influence of Plastic Deformation in the Austenitic State on the Kinetics
of the Development of Temper Brittleness of the Steel 3OXhGSA.
which quenching was preceded by plastic deformation in the
austenitic state under conditions which excluded reerystal-
lization of the worked austenite. To this end a big batch
of 8pecimens was treated by heating to 12500C, cooling to
900 C, rolling, and quenching the specimens immediately after
they had left the rolls. Rolling in all experiments was
carried out with 'a 'reduction of area of 35% and at a
speed of 1.5 m/min. Oil was used as the coolant. The
control specimens without plastic deformation were also
oil quenched after heating to 12500 and cooling to 9000C.
The specimens after normal quenching, and those having
undergone plastic deformation prior to quenching, were
tempered at 5500C for 5, 24 30 minutes, 1, 29 4, 8y 16,
32P 64, 128, 256 and 512 hours, and subsequently water
quenched. Toughness tests were carried out on notched
specimens 10 x 10 x 60 mm. In Fig.1 the dependence of
toughness and hardness of steel 3OKhGSA specimens on the
Card 2/4 length of tempering at 5500C is shown (1 - after normal
quenching: 2 - after plastic defatmatim und quenching). Fig. 2 shows
kl--~

67716
SOV/126-7-3-12/44
Influence of Plastic Deformation in the Austenitic State on the Kinetics
of the Development of Temper Brittleness of the Steel 30KhGSA
the same relationships for the same steel at the same
temperasure (I - after normal quenching and tempering
at 650 G, followed by slow cooling; 2 - after plastic
deformation combined with quenching, and temperin& at 6500
followed by slow cooling). Fig.3 shows the dependence of
toughness for specimens of the same steel on testing temper-
ature (I - after normal quenching; 2 - after plastic oc
deformation combined with quenching, and tempering at 550
for 2 hours). In Fig. 4 the same relatiozicahip. its in Fig. 3
is shown (1 - after normal quenching; 2 - after plastic
deformation combined with quenching and tempering at 5500C
for 512 hours. The results confirm the deduction about
the stability of the brittleness-offect-doerease as a
result of combining plastic deformation with quenching
whereby recrystallization of the worked austenite is
prevented. This enables the conclusion to be drawn that
the observed decrease in temper brittleness is not the
result of a change in the kinetics of the precipitation of
Card 3/4 phases or compounds which are responsible for the development
L-K

67716
SOV/126-7-3-12/44
Influence of Plastic Deformation in the Austenitic State on the Xineties
of the Development of Temper Brittleness of the Steel 3OKhGSA
of this type of brittleness. The results obtained wafirm
the assumption made earlier, that plastic deformation of
steel of the austen:~tie state brings about such changes in
the crystal latticeibof intergranular transition zones and
regions adjoining them as are capable of changing the
condition and form of precipitation of phases and compounds
which cause the development of brittleness (Ref.4).
There are 4 figures and 4 Soviet references.
ASSOCIATION: Institut fiziki metallov, AN SSSR (Institute of the
Physics of Metals, Ae. Be. USSR)
SUBMITTED: November 16, 1957.
Card 4/4

22547
Lio(t'j 1H is, 14)74 S/129/61/000/005/003/003
B073/E535
AUTHORSz Sokolkov, Ye. N., Petrova, S. N. and Chuprakova, N.P.
TITLE. Influence of Plastic Deformation in the Austenitic
State on the Properties of Constructional Alloy Steels
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
1961, No.5, pp.12-14
TEXT; The authors investigated the influence of high
temperature plastic deformation on the mechanical properties under
tension at sub-zero temperatures. In earlier work (Ref,l:
L~ V. Smirnov, Ye. N. Sokolkov, V. D. Sadovskiy, Trudy instituta
fiziki metallov; No.18, 1956; Ref.2: Ye. N. Sokolkov, L.V.Smirnov
Metallovedenlye i obrabotka metallov, No-3, 1957) it was establish
ed that thermomechanical treatment weakens the tendency to temper
brittleness. M. M. Shteynberg and A. A. Popov (Ref.3: Zavodskaya
laboratoriya, No.11, 1952) found that constructional alloy steel,
which is in the temper brittle state, fractures along the
boundaries of the austenitic grain is a result of tensile stresses
applied at low temperatures. For the experiments a Cr-Mn-Si
steel of a high sensitivity to temper brittleness was chosen
(composition, 0.30% C, 1.o6% cr, 1.2% Mn, 1.05% Si, 0.02% P,
Card 1/ 4

22547
Influence of Plastic Deformation s/i2g/61/000/005/003/003
E073/E535
0.023% S). Plastic deformation was carried out at goo, 1000,
1100 and 1200'C on a laboratory hand-operated rolling stand., The
rolling speed was 5.7 m/min, the reduction was 30%. Blanks
10 X 10 X 55 mm were heated to 12500C in graphite tubes and held
at this temperature forone hour (the increased heating tempera-
ture ensured observation of failures); following that, the blanks
were cooled with the furnace to 1200, 1100, 1000 and 9000C. A part
of the specimens were then subjected to rolling from these initial
temperatures, whilst another part was quenched in oil. For fixing
the structures produced as a result of plastic deformation, after
rolling the specimens were rapidly (0.3 to 0.4 sec) quenched.
From both types of specimens tensile test specimens of 3.5 mm
diameter were produced. Preliminarily all the blanks were
tempered at 5500C for 2 hours. The tensile tests at -195% were
carried out in a special attachment fitted to the test machine
WM-L~P (IM-4R), The results are plotted in Fig.1, the real
breaking strength s k' kg/mm , the elongation y,%, 6,% vs. hot
working temperature, "C; 'whereby the dashed lines apply to
ordinary quenching (without hot working), whilst the continuous
Card 2/ 4

22547
Influence of Plastic Deformation ... S/129/61/000/005/003/003
E073/E535
lines refer to the specimens whicii i '~,-ere -subjected to thermo-
mechanical treatment. It can be seen that t1ye strength and
ductility at -1950C increases most as a result of thermomechanical
treatment at 9000C; mechanical deformation at higher temperatures
leads *to deterioration of the properties. Similar results i.,ere
__ -~r : (20Xh'_K3) -;3s) .
also obtained for the steels. ~ - !: -. , _- - , /,;- ~, - (36m,,,
The microstructure i-.,as also studied afters each regime of thertno-
i,zechanical treatment. After ordinary quenching, the fractures
-show boundaries of austenitic grains, whilst after therizioi!icchailical
treatment the fractures show intracrystalline planes and only in
individual sDots can austenite grain boundaries be detected. An
increase in the temperature ok the thermomechanical 'treatment to
10000C and hi-her leads to a recr.N~stallization of the wor'
hardened austenite.which begins at the boundaries of the austen-
itic grains. With increasing recrystallization, the ductility and
the strength decrease. The' exDeri-,,~ients have shoin that as a result
of the therit-ot-iiechanical treatment the brittle strength of the
austenite grain boundaries increases, reducing the temperature of
transition to the embrittled. state. There are 1 figure and 6.
Soviet references:
Card 3/4

LIX
Influence Iof Pla-~Illic Deformation ... S/129/61/000/OG5/003/003
RO?3/Eq35
ASSOCIATIOIN: J~stitut fizilri metill'ov AN SSSR
(institute of Physics of 'Metals AS USSR)

12

Fig. 1
18

ItO 4 4

vo labra Ilro T

34-53h
S/6r_ 9/.61/1007/.000/021/044
D21 7/D3 013
AUTHO-HS,~ Sadovskiy, V.D., Sokolkov,_,Ye._N,, Lozinskiy, M.G.,
Petrova, S.N., Antipova, Ye.I,,. Gaydukov, K.G,, and
Mirmel'shteyn, V.A.
TITLE: Influence of thermo-mechanical treatment on the high
temperature strength properties of aus-uenitic steel
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Issledova-
niya po zharoprochnym splavam, v~ 7. 1q61p 202-209
TEXT: A complex alloy steel of the austenitic class, widely used
in industry for manufacturing components for high temperature ser-,
vice, was studied. During ageing of this steel, the complex chromi-
um and vanadium carbides responsible for its strengthening are pre-
cipitated. The material was heated to 1180 - 12000C and rolled at
1000 -- 11000C at a speed of 5.7 m/min. After rolling, the billets
viere immediately water quenched in order to prevent recrys-talliza-
tion. The cross-section of the billets obtained was 11.5 x 11~5 mm
their length, 70 mm, and the reduction due to rolling, 25 - 30
Card 1/4

S/.659 /61/.007/1000/021//044
Influence of therma-mechanical D217XD303
Control billets were heated simultaneously with those chosen for
thermo--mechanical treatment, and were subsequently quenched from
the above temperaturt, All billets, whether thermo-mechanically
treated or only heated and quenched, were aged to a hardness of 310
- 320 HB~ After heat treatmentg specimens for two series of -'U-ests
were made from the billets. One series was used for stadying struc-
ture during high temperature extension in vacuo. This also enabled
%he degree of deformation to be determined and photographs of the
same portion to be taken at various stages of testing. Testing was
carried out in a IMASh-5M machine at 9000C and a stress of 9.5
/mm', using spe-cimens of 3 x 3 mm cross-section, heated by dire;_--t
passage of current. The second series of tests, in which K.1~ Tere-
khov participated, consisted of the standard tests for long-term
strength at 6500C and stresses of 35 and 38 kg/mm2g as well as al
70000
. -and a stress of 32 kgi/mra2. For this purpose, spe3imens of
.-iorking portion diameter of 5 mm and 50 mm length were used. The
microstructure of each specimen was studied in conjunction with
these tests, particularly any peculiarities in structure appearing
after t hermo-mechanical treatment as comDared with normal quenching.
C a r d I I/

S/65 61/007/000/021/044
Influence of thermo-mechanical D21'I7YD303
The distribution of deformation along the length of the speoimeng
the intercrystalline and crystalline plasticity and the formation
and propagation of cracks during fracture were given particular
attention. It was found that high-temperature plastic deformation
of the steel investigated, under conditions in which recrystalliza-
t-Jon processes are suppressed (thermo-mechanical treatment)" leads
to a considerable increase in long-term strength. The beneficial ac-
t1on of -chermo-mechanical treatml~nt is associated with structural
charar.teris-t-l-s of the steel which arise during high temperature
plasti:~ deformation and are fixed by cooling at a sufficiently high
rate. Such characteristics are the complex Geometry of grain boun-
daries, grain fragmentation and further refinement of the fine cry-
stal structure. These structural characteristics of the steEl re--
tarded the development of fracture during creep, since (a) the cha-
racteristic serrated grain boundary structure retards the amalgama-
'tion between micro- and macro-cracks; (b) breaking-up of the fine
crystal st~ructure, and an increase in the density of immobilized
dislocations render plastic deformation within the grains more dif-
ficult. There are 5 figi3ras and 16 references- 15 Soviet-b-loc and
Card 3/4

S'/659,/61/007/000/021/044
Influence of thermo-mechanical ... D217/D303
- r.on-S(,-viet-bloc. The reference to the English.-language publica-
4ion reads as followsg P.W~ Davies and J,P~ De*nnison, J. fnst. Me-
tals., 87, 4, 1956.
V~
Cara 4/4

.SOKCLKGV -E-N-[Sokolkov, Ye.N.1; PETROVA, S. N.; CIUPRAKOVA, N. P.
IChuprakova, N. P.]
Influence of austenite plastic deformation on the properties of the
structural alloy steel. Analele metalurgie 15 no.4:124-127 O-D '61.
(Austenite) (Steel-Heat treatment)
(Deformations(Mechanics)

33464
S/129/62/000/001/007/011
A L'~u E073/E335
AUTHORS: Kishkin, S.T., Corresponding Member of the AS USSR,
Lozinskiy, M.G., Doctor of Technical Sciences,
Bokshteyn, S.Z., Doctor of Technical ScieAces,Professor,
Sokol~~ov, Ye.N-, Candidate of Technical Sciences
TITLE. influence of high-temperature plastic deformation
on the mechanical properties of heat-resistant
nickel-base alloys
PERIODICAL., Metalloveder-iye i termicheskaya obrabotka metallov,
no.l,.1962, 38-4o + I plate
TEXT: Two Ni-Cr-base alloys were investigated: the low-carbon
?M-4376 (E1437B) alloy of the standard composition and the
containing 0.12% C and additions of W and
1~4617 (E1617) alloy,
Mo. The alloy EI437B was subjected to the following thermo-
mechanical treatment: blanks of 16 mm diameter were first soaked
for 8 hours at 1080'C and rolled at this temperature at a rolling
speed of 4.5 m/min to 30% reduction. 0.2 to 0.3 sec after
deformation, the blanks were quenched to supercool the austenite-.
Card 1/4

33464
Influence of
S/129/62/000/001/007/011
E073/E335
and to retain the structure, produced as a result of high-
temperature plastic deformation. The blanks were then
aged at 7000C for 16 hours. Blanks of the alloy E1617 were
heated to 12000C and stamped in a press, so that an average
reduction of 30% was achieved; this was followed by quenching
in water. The blanks were then aged at 8000C for 16 hours.
The results of static tensile and impact tests at room
temperature are given in Table 1. Studies of the influence of
thermomechanical treatment on the creep strength of austenitic
steels revealed that recrystallization should be prevented
during high-temperature plastic deformation since it would
cancel out the beneficial effects of the thermomechanical
treatment. Microstructural investigations correlated
with the results of mechanical tests indicate that the increase-in
strength and'ductility occurs even if recrystallization has not
been fully suppressed. The increase in strength is
attributed to an increase in the quantity of the
carbide phase, to changes in the finely crystalline
Card 2/4

33464
S/129/62/000/001/007/011
Influence of .... E073/E335
structure of the material and to texturing. _The large increase
in the ductility of the investigated alloys is obviously due
to the abs ence of intercrystalline fracture. The following
participated in the experiments: N.I. Korneyev; T.A.Gordeyeva,
Ye.I. Razuvayev, O.N. Podvoyskaya, M.N. Kozlova,
L.M. Strizhevskaya, T.A. Volodina, N.F. Lashko, E.V. Polyak,
G.N. Korableva, A.V. Bulanov, M.I. Spektor and I.G. Skugarev.
There are 2 tables and 7 references. 4 Soviet-bloc references
and 3 non-Soviet-bloc. The three English-language references
mentioned are: Ref. 4: E.B. Kula, J.M. Ohosi - "TASM", v4,52,
1960; Ref. 5: DJ.Schmatz, J.C. Shyne, V.F. Zackay - Metal
Progress, v-76, no. 3, 1959; Ref. 7: E.B. Kula, S.L. Lopata
Trans. AIME, v.215, 1959.
Card 3/4

Influence of ....
Table 1-
33464
S/129/62/000/001/007/011
E073/E335
Mechanical Properties
Alloy Treatment 6b.22 'r-9 6, %fg a HB
2 1) 2 k' 2 (d,
kg/on kg/mm, % % kgm/cm omn
MW)
B1437B Standard (reference
specimens) - 97.0 25-0 20o9 -
TMO If - 119 32.0 30,7 - -
Standard (reference
E1617 specimens) 71.7 103.7 14.6 io.i 1.8 3.6
Time 93.8 129.6 31.2 25.9 7.8 3.35
x Plastic.deformation of supercooled austenite
followed by conventional hardening and tempering
Card 4/4 treatment.

37728
S/180/62/600/002/001/018
E193/F,383
AUTHORS: Boksht Cyn, S. Z. , Kishkin, S.T. , Lozinskiy, M.G. and
Sokolkov, Ye.N. (Moscow)
TITLE: Thermoniechanical treatment of a chromium-niclcel-
manganese austenitic steel
PERIODICAL: Akademiya nauk SSSR. Izvestiya. 'Otdeleniye
telchnicheskilch nauk. Metallurgiya i toplivo, no. 2,
1962, 15 - 21
Tz;-"T: The, so-called, "thermomechanical treatment" (TMO)
cousists essentially of.combining plastic deformation at
.c;:;,:)erat1ures above the recrystallization temperature with
cluenclaing under conditions precluding recrystallization of the
plastically deformed material. The effect of this treatment on
'Alic structure and properties of various materials has already
been studied by other ivrorkers. Some additional data on TI-10
of austenitic steels are presented in the present paper,-;,rith
--)articular reference to the properties of these steels after
..l
1~'O to the ageingtreatment and to some characteristics of the
diffusion processes. The ex'per:Lments were conducted on chromium-
Card 1/8

S/180/62/000/002/Ool/ol8
-L:icr;-.iomechanical treatment' .... E193/E383
nic'.
kel-manganese austenitic steel 9LA481 (E-III81) specimens,
and 60 tai;i in diameter, the former 150 and the latter 250 Mm
1 on,,- The plastic-deformation part of TDIO was effected by
I-ollill'; at 2."1 I;IAiin iti the ca.-io of specinions, Go mm iii diamcLor
al-,d at 4.5, 7.5 and 13.5 m/min in the case of 13 mm dia-,-,ic'4l-er
oils. 25 and 30% reduction vras given in each case.
_~)r Cs s Od
-:-"Ystallization of the 13 mm diameter specimens was sup-
irm:-.ediate quenching in a water tank mounted on the rolls
the tir-,ie interval between completion of the rollint
o-3-----ation an6 quenching amounting to 0.2 to 0.3 sec. Rapid
cooling of the 060 cum diameter specaciens was attained uith the
aid of a specially designed spraying device. Preheating of
tt'la test -,-pieces for rolling -,q-as done in air in an electric -
the prahGating taimperature and time being 1 180 OC an,!
2 hours, rospoctivoly. TMO o:6 sinall (15 = diamoter) test
,)icaos was 'carriod out a~'ter cooling them from 1 180 to
OC. I n tho case of large (60 nim, diameter) test pieces
T4':O -.-;as applied at t:-.e preheating temperature and after cooli-.nr-
card 9-/3