SCIENTIFIC ABSTRACT KOGAN, L.G. - KOGAN, L.M.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000723610013-8
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: September 19, 2001
• Sequence Number: 13
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

-@,, --I'
%'r." -0, 7 .1" - ,

Construoting on the basis of ejertric-model data the current lines
and current pipes in a romervoiy. consisting of several =irorm
sections possessing various paramiero. Nauoh.-tekh. abor. po dob.
nefti. no.2006-41 1634. (MIRA 17s6)

KOGANj L,.G*l KWUVt V#P,
Electric modeling of propane drive vith subsequent Injection
of dry gas for a nine-point system of well'apacingi Trudy
VNIX noAM67-181 .063 MIRA 1737)
Effsot of the nonuniformity of reservoir structure with rea-
Peet to parme4bility on the conformanco factor and other para-
meters of development# lbidosI82-191

Caloulating the resiotancen of elsotrio modela 6f nonuniform media.
Nauoh.-tekh. abor., po dob, nafti no,2206-40 164, (MRA 17:9)
1, VeasoyuzW neftogazovyy nauohno-iseledovatellakiy institut.

XOGOO-LAtj ANDREMAj We
Electric mods ling of the developmant of a bed consisting of bands
of varying permeability. Nauch.-tekh. abor. po dob. nafti no.24s
95-105 164. (KM 17 10)
Vesaoyu=yy neftegazora nauchno-inaledovateltakiy institut.
73
atvi

ACUSSION NR: ATW41656 S/2604/64/000/051/6i@i@@
AUTHOR: Kogan, Le I*
waves during the c@nt I nuous
'TITLE: Method and apparatus for r-ecording refracted
movement of a seismic exploration vessel
Zz
:SOORCE: Moscow. Vsesoyuz" nouchno-issledoviteliskly Institut geof)ZIcheskikh
metodov razvedki. Razvedochns a tpr?m 1 4.0 43-48
,Y*s ovays coflzika, no. 51, 196
9
1; JOPIC TAGS:' seismic wave, selsml@fexploratlon, seismic refracted wave, seismic
fIIterIhq,-seI&aograph0 marine selimography,'piezoolectric detector
ABSTRACT: Methods and apparatus are already available for recording ref I acted...,
seismic waves during the continuous@movement-ofe,selsmic exploration vessel.. f
;-Since 1958, the HINGE VNIIgeofIzIk1 has been seeking a method of using the refracted'
.-waves under similar-conditions, This'artIcle describes the method and apparatus
now de4eloped for this purpose. 60hasis Is on a description of th string of ple-
zoelectric detectors-towed behind the vessel (shown In Fig, I of th: Encfosure)o
Was necessary to attain a high'absolute sensitivity of the plazoelectric,channel-0,.
this was accomplished by usin titanIum-harium pressure detectors having an
.9 20
'absolute sensitivity of,3&0-4*0 0-v/bar. *This made a high sensitivity Increase
sp,lblp and mad* It possib,le to match.the plezoelectric.channel with the Input of,
'Card

4,
If
ACCESSION HRI AT00656
the seismic station amplifler; this Is very Important when-recording low-frequeW
0
refracted waves. The changes In specifications for the filters of the SS-26-i5l
seismic station are described In detail; the maxims of,the,frequency ch4roct*r(;tIc6,,'
of the amplifier filters were shifted Into the region of low frequencies. Various
icomponents'of the modified seismic' station are described, and the method for sh6ot-
Ing profiles at sea by*the refracted waves method Is discussed. When the rate of
li movement of the sal.smic exploration vessel is 4-5 kn/hour the explosions see set
off at a rate of-6 or 7 an h6uro 'When recording Is done at short distance$ 64
charges used weigh up to 50 kq and the @xploslons-pre sit off at the rate of 10-12
an hour. Ways In which the productivity of,such exploration work at sea can be ln-o@':
creased are suggested. "The following.persons participated In the deve,lc@ment and
adoption of-the.new method for reckirding..rafracted waves during this movement.of a
seismic exploration vesseIr A* A* Gagel*gants, So P.-Vartanov, V. Z. Zonov, Bo A
144 Zakharbv and G -So Zolotarev", OrIg.'erto'hass 2
ftndaranko Vo Vo-Bokun# 0,
formulas b e-
4 f I gures -and -1 to I
-icl
ASSOCIATION:' (All-Union, enti-fle. Research'instltuto of Geophysical Mothods'of'
Exploration) Vsosoyuzny*y nouchn0olssledovatellskly Institut,gooflatchaskilth.
meto
do4 razvedki, ftsew
2/4"
carg
_Ott.

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karadof
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a on steel crystallisation ud
]Iff act of certain, goal addition GIONOnt ovedoi fiso mt. no.[11:225-274
recrystallization Processes. Probl.mitall
149,
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loLaborstarLY& fasovykh -Provr gkoge, instituts hernor OstAlurgsto
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,!_-ry J-
Catogory t USSR/Solid State Fhysica Phase Traneformation in E-5
Solid Bodies
Abs Jour t Rof Zhur Fi@ika,@. No @3, 19
-57, yo 6618
Author' I Kogan. 1. gntin'i Ili!
Dittio,ulty-Solubla-Cerbidoo-
onitho Dec-omposition-vt4ustonite.
Orig Pub i Probl@ motallovadi'i ftz@ votellov. Ob. 4, 1955, 251-286
Lbstract i When hardonin f 'd"d-rdinary hacLt treating temperatures
g. r iv
(900 1000 #' -tho:v.osiunco of. such atrongly-earbida-forming
alements as Tit-Ni-Zr ''Nb* --endIa-reduces the hardonability
V I
of'tho carbon stool, owing,to tha:'fomption of quite stable
carbides b@ those elements. A portinI transCormation of these
Carbides into oUstanito when hosting to 900 -- 1000O.can-be
accoraplished the -steol - idth -manganese (1,5 .6-. ..1
2.5%), t' ;n --this - C'66 e; -. oddition of titanium to manganese stool
incroabos co6sidott-blyAho stability or;tho austonito in the
@Qerlito'kd_intormdd i6torogi-ons.- Alloying with titanium
aloo loads to a sharp isolation of the poarlito and middle
v:
7

-46JAVVAMUA&=%0.LW1@ W@... WAAW '@&OW6.&WWWA-6 Z4
tW'fr6a-a9s-- o -A-Uste,
f- ni
-Chtomiua -.0R7.-T,=t0-t0
*A' -'@riet-alld4i@-sb 1955-, 2774
Orig- Pub A Pro M G-.t;e--l 16
Abstrect t ThemothoLd of- redio@Aive. isioto'pbs' Was u so d 'to dotormine the
contents of, .Or, and 4! in--'tho .carbide' phase in steels with
2. with' 1002, -0 d 0
1.18% 0 4@%.Or' @snd an -78% W respectively
in the prooeBaL Of austanito at the tom-
poraturos of the pan Lr1ito and intoreodiato regions. In the
Process of doco mpooition in the pearlito region, the contents
of thor1loying olome 'nto in the carbides exceed their contents
in stoolby'a faotor_OfL 3 -- 5 times. The results obtained
prove thattho de@,ompovition of tho austonito in the pearlite,
region is connected with the need for diffusion redistribution
of the tungsten. It is shown thet rate of socondery diffusion
Cord 1 1/2

81510
9,5-0 0 SOV/1,37-59-5-10755
Translation 'froms Referativnyy zhurnal,- @Metallurglya, 1959, Nr 5, p 184 (USSR)
1111gan-, L-1
AUTHORS: x llat!!L.R.I.
mu: On the Thilor'7@of Intermediate-Austonits Transformation
PERIODICAL: V ob.'s 14at*r1aly Nauohno-tekhn. konferentaii po probl. zakalki
vgoryaohikh sredakh-,-i prom6thutoohn. prevrashchenlyu austanita,
Nr 1. Yaroelayll, 1037, PP 3 - 28
ABSTRACT: Information is given on results of investigations into pecullari-
ties of Intermediate transformation of austenite and on the nature
of phase formation.' It is noted thit-intermediate,transformation
Is comeo ted with a redistribution of C and I-oQL martensite-trans-
formation. Redistribution of C In the austenite precedes the
T --lo M transformation. The higher the temperature of intermediate
transformation, the sharper are the changes in the period of the
residual aust6nits lattice, L.e,, the higher Is the degree of
diffusion redistribution of C in the austenite. Relief formation
Is a charaoteristio feature of Intermediate transformation. ft-1he
Card 1/2 m&ximum temperature of the intermediate transfomation, in the given

AUMRS:Kogany ..and -Entiny- R,I* 3.26-2-24/30
ion of -awtenite
TITLE: Redistribu-Won of carbon during transformat
in the'medium range'. (Peraraspredeleniye urlerods, pri
prevrashoheaft'austeuita, v aredney oblastiT.
PERIODICAM "Pisika-'MeW (PbYsice of metals
061 U" -210.2v 195-11 PP-360-368 MOSR)
and 0
ABSTRACT: Recent experimental ddta, enable to characyterisi follows
individual elementary processes which bri% about,, axtstanite
transformation inthe medium range of temperaturesi the
austenite transformation takes place without any appreciable
redistribution of the alloying elements; this follows from
numerous results of analysis of the structure and composi-,
tion of the carbide-pbase which indicate that,apart fi-om
the dependence:on.the structurevf the equilibrium carbide
phase-leementitelforms in the medium temperature.range, the
content'inalloying elements of which@oorresponds a roxi-
mately to their average content An the steel (6 to
Measurement of tire period of the crystal lattice ofthe.-austen-
its indicates that transformation in the medium temperature
range.is linked with redistribution of the carbon (9 to 11);
Chrd 1/T intermediate transformation can be linked with,enrichment as
well as with 1moverishment-in carbon of the residual aus-
tenite. Aust;,@Iie transformation in the medium temperature

f
Redistribution of carbon dui-ing. transformation -o usten,
ite In the.medium,range'. (Cont.) 1@6- 24t.3-A
Card 2/T
range.is accompanie&by the-formation of a characteristic-
relief on.the polished. surface of the out and this indio-
ates a regular character of the displacements of the atoms
at the phase-boundary and a coherence of the phases (11-13)".
Formation of a relief during the transformation is oharac-@
teristio both for allov and fbr carbon steels (11)'.' It was
also - shown by Kogan(16) ftt even in practically carbon free
iron alloys alloyed witii various elementsv the y to a trans-
formation at temperatures below 500,- 400 C can take..place
only-as-martensitio transformations. All these data-indt-
cate that.austenite transformation in the medium tempera-
ture range-represents a martensite mechanism of -T to a
trdnsform&tion and-therefore austenite transformation in
the medium temperature range has.to be interpreted as 8,
combination of the processes of diffusion redistribution
of carbon in the emetenite and of a martensitio Y to a
transformation in sections of the austenite with reduced
carbon doncentratibnos.,- In'this paper experimental results
are given on the character of t1%e process of carbon re-
distribution as a-function of the steel composition (content
of 0 and of alloyinj elements) and-also the results obtained

Redistribution of carton-during-transformation of auStan-
ite-in the medium range'. (Cont. 3.26.2-94/30
of:tho.ohanges in the carbon 6oncentrat
Jaii i@ t Ih" austanite . as a function of the. temporature and
duration, of transformation of the anstmAte in the medium
temparat"e range'. The.ldttice period of the austenite
after its partial transformation in.the medium.temper&ture
range.was measured for a namber of steelog the chemical oom@-
PO8itiOMB Of Which.'(for 12 steels) are entered in Table lo
Y,361'..- In.para@l the.change of the average--period of the
austenite litiice as a runotion of trangformations.in the
medium. temperature -,rdnge -is; studied on steel. specimens with
an a oimatelyequal chromium content (3','45@_ Y-15 and
t I P r-
,'.,.4jfb. 'differizig carbon. contents (1.44, 0.98 and 0.54%)',
n a a.2 the same relations @ar a studied for the steels
118T(1'18% dr 3P.58%'Ka) and 48r4, (O@48% C, 4r.3S% UnY. In
pa. t@; same relation was studied,Zn the steels '301.0,2
@a .3
00@ C and- 2','9% Al) -and -79102 (0'.79% 0 and 2A% Al) a-. In
para.4 the changes itL-:the lattice period of the residual
austenite are compared for. partial transfo=ations 131 the
Card 3/7 medium temperature range for steels with approximately equal
carbon contents. The authors arrive at the following aon-
olusions: in the case o'f'alloying with Cr. Nh and Ni the

Card 4/7
Redistribution of carbon d:uri iransf6rmatjon Of' t
473-0
ite 3 in the medium Ange' (con 1Z-2-2 ans
P
degre'e of carbon enirichment of the'residual austenite as 'a
result of the austenite transformation in the medium tem:-
perature ral@ ' depends fundamentally on the carbot,co t
, Se Uten
of the steel. The degree of *change of the concentration of
carbonin the-austenite (for increasing as well as decreasing
0 conteirts) will be.the higherp the higher the traneror-
mation teMerature-it the medium range ,. Pbr,steels for
which carbon enrichment of the residual austenite is a
characteristic featurej the curves of the changes of the
lattioe period of the residual austenite as a tanotion. of
the transformation time in the medium temperature range
and the curves representirg the kinetics of transformation
are similar. For steels for which a decrease in the carbon
content of the austenite is characteristio,the sharpest,
ohamge (decrease) of the lattice period is observe'd-before,
the a phase begins to separate outp ipe., in the initial
stages of transformation@. This is obvious from the X.-!ray
exposures taken directly at the transformation temperatures.
The auste'nite transformation in the medium temperature range
is characterised by-'a.redistribution of the carbon in the
austenite and Subsequent martensift transformation in these
ffi"1111 I FIN-M,

Redistribution ofearbon during tran formation of austem,-
ite, in the medium. 'range". (Cont.. 126-2-A/3D
austenite sections which have a reduced carbon ooncentra-
tion:. For temperatures corresponding to the medium temp-.
erature range the formation of nonuniformities as regards
the carbon concentration In the austenite is advantageous.,
from the thermodynamio point of view since it brings about
a reduction of the free.energy of the system'. The direct-
ion-.of the process of redistribution of carbon in the
avstenite at temperatures of the medium temperatnre range
is determined by kinetic factors"# I 'n steels containing
0' 3 to. r.6% Olmovement of the carbon,into the remaining
P@;t of the austenite may prove kinetically more.advantag-
eque than the formation of comentite1whichrequires a car-
bon concentration increase to 6.7% andiconsequentlysit -
requires diffusion from .1 distant spots'. In steels contain,_
img O.7'io 1% Of in, which no changes of the average,lattice
perio& of the residual austenite are observed daring trans-
formation in the medium temperature ranget removal of oar-
bon from the sections with reduced concentration into the
Card 5/7 remaining part 9fthe austenite and separation of cementite
is equally likely. Interaction between the atoms of Poo 0
and of tlie., alloying elements can change appreciably the

Redistribution of carbon during transformation of. Owten-
@-2-24/
ite in:the-medium a! '(0ont
degree ~of-'iho~'V*Siiii~tiibtiti'6jm-.':df -0 in, the@ austenitev-.1or
inBt4noe, alloying *ith _81jeade,to avery Ponsidbrable L
carbon -64ricltnezt. of'1h6 -1 residual austehits. - Even in high
carbon atisel which Is alloyed'with Sip transformation or
the-austeniteAn the'medium temperature range involves an
increase in.-fte caton'. contbnt In the residual austenite by
0-5 to 04%, . Thereby,the spedific influenice of Si Is ex..
piained bythe inhibition of the processes of carbide for-
mation. -The higher the transfozzation temperature iii the
medium temperature ranget the more will the carbon content
be lowered in thow austenite sections which are subsequently
subjected to'martensitio transformation@i This conclusion Is
confizmed, by the. dependence of the degree of the change of
the-carbon concentration in the austenite 'oji. the transfor-
-----matiou-temperature--,(1*r- -aa- equal- -degree -of- traxwfoxm
ation)r
Self -braking of the reaction in the medium range is not
linked with a redistribution*of the carbon and is obviously
Card 6/7 the result, of the martensitic mechanism of y to a trans-
formations. -The influence of alloying elements on the
kinetios.of transformation of the austenite in the medium

AUTHORS: Kogan, L!_I@.and Entin,-R. 1. 126-2-20/35
,TITLE: On secondary hardening of structural steels.
(0 vtorichnoy zakalke konstruktsionnykh staley).
PERIODICAL: Fizika Metallov i Metall .ovedeniye, 1957, Vol-5s N0.2t
pp. 349-354 (USSR)
ABSTRACT:' The causes are investigated of -secondary hardening of
structuralsteelsLin conjunction with experimental
investigation of the changes of the crystal lattice
period of residual austenite. In s8me structural.and
tool steels tempering at 500 to 600 0 brings about a
transformation of residual
secondary hardeningg, i.e.
,
austenite into martensite,during subsequent cooling.
Secondary hardening in structural steels was observed
during tempering only if the hardening was effected
under conditions ensuring partial transformation of
austenite in the medium temperature range. Investigation
of the secondary hardening was effected on the two
steels 34XIU2.and 73XH3 I the compositions of which
are as follows: 0.34% 09 2.5% Big 1 08% Mn, 1.89% Or and
0'.73% C 0 3% Big 0.78% Mn, 0 7% Cr: 3.48% Ni
respectiveiy. The heat treat@;nt of chromated specimens
Card 1/4 of 3x5x25mm was effected in an"anizometer"; the

'On secondary.hardening of structural steels. 126-2-20/35
specimens were heated in the furnace to 1000 and 900oC
.respectively for six minutes and then 8ransferred into
a tin bath which was heated to 300-400 0 and finally
quenched in oil. -Followingthat, one of two specimens 0
was heated in-the.oil Wh of the anisometer to 500-550 C
and then cooled to 280 C inside the bath with the heater
switched off and finally transferred to an oil bath of
the same temperature in which it was cooled to room
temperature. Due to such slow cooling below the
martensitic point a maximum quantity.of residual
austenite remainel in the specimen which facilitated
measuring the period of the crystAl lattice. Duringthe
process of cooling, the deflection of the light beam of
the anisometer was recorded and from the obtained data
the cooling curves were plotted which were compared with,
the cooling curves obtain d for a specimen of the same
steel containing 100% of the maGnetic phase. A bend in
the cooling curve was taken as an indication of the
existence of a secondary hardening, After the heat
treatment the specimens were etched and investigated by
meens of the X-ray ionization instrument YPC-50-H at
Card 2/4 room temperature. The period of the austenite lattice

On secondary hardening of structural steels. 126-2-20/35-
was measured before and after tempering on the line (200);
the absolute error amounted to 0.0026 M, The experi-
mental results are entered in tables and graphs. It was
found that secondary hardening is linked with a reduction
of the carbon content and possibly also of alloying
elements ig the residual austenite during tempering at
500 to 550 C. A qualitative-oorrespondence was observed
between the degree of drop of the carbon concentration
in the residual austenite andmthe intensity of secondary
hardening. In structural steels a preliminary condition
of secondary hardening during tempering is the occurrence
of partial transformation of austenite in the intermediate
range during hardening. Such hardening leads to a
considerable increase in the carbon concentration of the
residual austenite an@ therefore during subsequent.
tempering at 500 to 5 OC a carbiae phase may separate
out from the residual austenite which will result in a'
reduction of the lattice period of the residual austenite.
In the case of steels with a higher carbon content
intermediate transformation during'hardening is not a
necessary condition for the separation of a carbide phase
during tempering at 500 to 550'0. It is possible that
Card 3/4 relaxation processes taking place during tempering play

On secondary hardening of structural steels. 126-2-20/35
an important role in secondary hardening.
There are 5 figuress 3 tables and 2 Slavie references,
,SUENITTED: July 24, 1956.
ASSOCIATION: Institute of Metal Technology and Metal Physics
TsffIIChM,
(Institut Metallovedeniya i ?iziki MetalloV TsNIIChM).
AVAILABLE: Library of Congress.'
Card 4/4

-A
129-58-5-16/17
Scientific-Technical Conference on Hardening_in Hot Media-and
'E_ n ar @Vlry-
-FEtii ealdfe dnsforma ion @f Auste ite (Y osl v
by high temperature tempering;
13) A full and even a:partial decomposition of the
austanite in the upper region of the intermediate range
causes appearance of a particular variant of irreveroible
temper brittleness which is characterised by a trans-
crystalline fracture.
Doctor of Technical Science-- R. I. Entin and L. I. Kogan
in.their paper "On theTheory of Intermediat6__T-rBR=iMW-
tion of Austenite" communicated experimental data on the
elementary reactionz, structure and composition of
transformation products of austenite in the medium range.
They pointed out that transformation in this range is not@
due to redistribution of the alloying elements in the
austenite b,it to diffusional redistribution of carbon in
the austenite, Depending on the.composition of the steel.,
and the transformation temperature an increase.or a
decrease of the carbon concentration in the residual
austenitemay take place,tihich is due to separating.out
of-carbides. In some ca-ses (for instance in nickel steels)
Card the process of carbon enrichment of the re-cidual austenite
4/29 at a later stage of the transformation is followed by a

sov/137-58-8-17683
Tr41nslation from: Referativnyyzhurnal, Metallurgiya, 1958, Nr 8, p 2 12 (USSR)
AUTHORS: Kogan, L. if , En,ti 'n,. R. 1.
TITLE: Transformation of Austenite in the Central Region (Pre, ra
shchenlye au.stenita v aredney oblasti)
PERIODICAL., Sb. t Y. In-t metalloved. i liz, metallov Tsentr. n. i in-ta
chernoy metallurgii, 195.8, Vol 5, pp 161-209
ABSTRACT: A survey of works dealing with the process of austenite (A)
transformation in.the intermediate region. The authors present
the results of experimental investigations of processes of redis-
tribution of C, the effect of partial intermediate transformation-
of A (ITA) on the kinetics of transformation during subsequent
-cooling, as.well as the results of investigations dealing with
changes in C concentration in the ck phase during ITA. The
investigations were perfor'med on experimental smeltings of
Mn, Cr, Si, Ni, V, Cr-Ni, Cr-SI-Mn,and carbon steels, as
well as on steels a 'Iloyed with Al. @ It is shown that ITA is
connected with a redistribution of C and with the martensite
'y - a transformation. By means of direct measurements
Card 1/3 of the period of the crystal lattice of the ;@tjs(en te A

SOV/137--58-8-.17683
Transformation of Austenite In the Gentral.Region
during the process of transfortnation, it. was established that the redistribu-
tion of C in A precedes the process of the Y -a transformation. , The
appearance of A zones, with.decreased C concentration makes it possible
for martens ite.transformation *p'rocess to occur at temperatures >Mn; A
zones with increased C concentrations may precipitate cementite. Alloy-
ing of steel with Si significantly increases the G content in residual A.
The formation of a relief.In the course of ITA is an'indicatior. of martensitic
character of the -y a transformation. The fact that certain steels ex-
hibit a protracted incubation period and the possibility of suppressing the
process of ITA during rapid cooling indicate that both these factors-Are
connected with proccsses of -dif WO lonal,oxepa ration and redistributio In of C
in A. The effect of Atioying elements onthe kinetics of the ITA Is deter-
mined by the manner In which they affect the diffusion rate and the diffusion
length of C. - The isolation of the intermediate region on the diagram of A
transformation is determined by a delay in the processes of formation of
carbides and polymorphous y -14. a transformation in the pearlite region.
whenever steel is alloyed with such elements as Cr, Cr and'Ni, Mo, W,
etc. As the temperature is reduced, the rates of diffusion of the alloying
elements and of selfdiffusion of F6--in the A become Very small and, under
these conditions, the process of transformation consists in diffusional
Card 2/3

AUTHORSt L-1, xQiAR_"d"R,* I, Intin BOV/24'58-6-3/35
TITLEs On the Nechanism,of the Isothermal Transformation of
Austenite In the Intermediate Temperature Range.(O
mekhanizme promezhutochnogo prevrashcheniya austenita)
PBRIODICALs Izvestlya akad'exii nauk SSSR, Otdeleniye tokhriiahaskikh
naukq 1958, Nr 6, pp 12-18 (USSR)
ABSUACTS The authors review the results of recent investigations
into those transformations of austenite which result in
the formation of bainite. They reject Cottrel's findings
(Ref 6) that martensite is not formed during these re-
a0tionsq and conclude that the bainite transformation
proceeds in two.-stages;: diffusion and redistribution of
the carbon.content occur during the firs-t--stage.-followed-
-
_ -by- a-mar tons iti CA -- -K@-trAhs_f6r_aui
t1vn. This. hypothesis
had been.advanood by the authors in an-earlier paper
(Ref 3) describing the results of an investigation of the-
isothermal transformation in stools whose composition and
code =mbers are given in Table 1. Some results of that
research are reproduced in Figs 1 to 49- in the form of
Card 1/7. graphs showing the kinetics of the transformation- (the tills

BOV/24-58-6-3/35
On the Mechanism of the Isothermal Transformation of Austenite in'the
Intermediate Temperature Range..
dependence of the.proportion of decomposed austenite) @and
the corresponding variation of the,lattice parameter.
However,. no general Aaws. could be formulated on the basis
@of the proviously.obtained.data and the present work was.
intended to verify the hypothesis that carbon redistri-
-bution did in fact precede martensitic transformation.
This confirmation was- to- be -achieved- by measurement: of ..the
carbon -con'tdnt_-_o_f_._.th6-4esultant *Lor ferrite phase, which
should, in accordance with the theory, have a carbon content
lower than the average of the investigated steel. In order
to avoid confusion due to the possible decomposition of -the
w. phase during the isothermal transformation, it was-
nece.saary to telect-steels in which complete transformation
occurred In the intermediate temperature range, and in
which martansite did not decompose below 400-4500C.
Consequently,, steels 24=3NU and 2382G3Kh2N2F composition
which were thought to.possess these characteristics were
'used in the present investigation. The coxpositions-of
Card 2/7 these steels were'-respectivelys
W

POV/24-58-6-3/35
On the-MechanismI-Of the'--Iso thermal Transformation of Austehite in
_the Intermediate Temperature - Range
1:2 2 2.10* Oil 2.9@%Mn, 1.85% Nit 1.61@% V;
0 23% 0 2.07%@'Sii 2.961 Mat 1.83% Cr. 1,,85% Nil - 1.,4% V@
The experimental specimens were investigated by hardness" I,
measurements$ and by magnetometric and X-ray difftacti0h:L
techniques, 04mples of forged material were chromium
plated.after vacuum homogenisation, They were then heated
in argon-to 11501DO I hold at this temperature for 4 to, 6
minutes and then transferred to the isothermal transfor-.-.
mation bath.vhich-was,saintained at temperatures.ranging,@.
from 150 to 350 C tor'a period long enough to ensure*the
maximum possible transformation at the given temperature',
The specimenswere thenquenched to room temperatu. i a,s@:@
10% solution of caustic "soda, The magnetometria m4asure@_,@-.@
@ments showed that'the austenite did not transform:,
isuLhormally at temperatures higher than 4000C., The
T.T.To curves for the two investigated steels are shown
on Figs.5a and 6a. As.ean be seen from the graphs
reproduced on Pigs 5b arA 6b, the proportion of the deabli-,
Card 3/7 posed austenite at @350, 300 and 2500C was 52 70 and 80%

IaVV/24-58-6 3/35
Onthe Machanism,-of--the.130thermal Transformation of Austenite
the Intermediate Temperature Range
respectively, 1he carbon content of the aL phase was-,
determined by an X-ray method developed by GJ, KurdyumoT..,
st aliij B.Z.'Mmiuskly and T,L Stelletskaya (Refs 0
.12,13) which-involved measurement of the vidth,of thel
line diffracted from the 211 planes. The variation of the-
width (a (in lo-3 radians)., and of Rockwell hardness number
(Be) of the'studied:steeJ97, quenched and tempered,for l,hr''.
at 200to 6500CV-.is entered in Table 2. The proportion of
the transformed austenite (X)% hardness (RO)p the-width
of the (211Y.linesi and the.estimated carbon content of
a
the at phase of steel specimens tempered for 30 minutes t'
various temperatures are@.given in Table 3. The data
reproduo6d in Table 2 indicated that decomposition ofthe-
martensite did not occur when the quenched specimens were
tempered for one,bbur at temperatures up to 50000. -Above
this temperature a &,crease of hardness accompanied:*A'
decrease in width of the (211) diffraction lines of the of.
phase. These, findings zonfirmed the suitability. of the
Card 4/7 selected steels for the purposes of the present investi-
gation, beewise thoy-showed that no decomposition of the

SOV/24-58-6-3/35
on the Mechanism of the Isothermal Transformation of AU3t9UitS in
the Intermediate Temperature Range
a phase would oacur during isothermal tTansformation
experiments all of vhioh wore carried at temperatures
below 35000 (Table 3). L-direot determInation of the
carbon content of the acphass in'the course of thetrans
formation thus became possible. The mean width,of.the
(211) diffraction line, determined planimetricallyt-was
found to decrease from 35 io-3 radians in the-Auenched
specimens to.,27010-!) Tadi;Z after isothermal transfor-
mation. These,widths were related to the carbon content
by a afi'L@1*99 of.. corresponding line-width determination's
made on the martensiftof steels containing the same, pro or-
tions of the alloying elements as the investigated steels,
and having carbon contents ranging from 0.05 to 0.20%,
(Fig 7). It.was found that the carbon content of the*w,
phase formed during isothermal transformation varied bet-
wean 0015 and 00'16%. The avera a carVon cbntent of.the
studied stools was-0.23 to O.R@, This decrease of 30%
in the carbon content was..considered-to be highly signifi--
Card 5/7 cant in view of a maximum possible experimental error of
only 4%. These findings were accepted as confirmation of

SOV/24-58-6-3/35
sothermal Transformation of,Austenite in
on the Mechanissi of the I
the Intermediate Temperat4re-Range
the hypothesis that'at the instant of its formation during
the intermadiate-tomperature transformation the carbon
content of the-oC,phase was already lower than',the average
carbon content of the steel. Consequentlylisothermal-
transformation of austenite must be preceded by carbon
redistributionl'which leads to the formation of domains
of highandlow carbon concentration- the domains of
lowest carbon
content are least stabieq and transform into
martensite. The stability of the other domains will-vary
with the carbon content, and any tendency to reject -
cementite at various rates will depend upon the temperature
and.the content of the alloying elementso
Card 6/7 There are 6 graphs, 3 tables, and 13.references of which,
11 are Soviet, kXnglish and 1 German.

SOV/129-59-6-w2/13-
AUTH098s No a L Li (Cand.Teeh.Soi.) and
(Dr. Teoh. Soi. 9 40fessor)
TITM Ce
rtain 4. verning the Transformation of
Residual Aijit'enite (Nekotoryye zakonomernosti
prevrashcheniy ostatochnogo austenita)
PERIODICALt Metallo-vedeniye I termicheskaya obrabotka metallovj
1959, Nr 6; pP 7-13 (USSR).
ABSTRACT: The authors investigated In detail the Influence of
partial intermediate transformation of.austenite on@the
subsequent transformation at lower temperatures for:the
steels 531[hM (0-53 CI-1.1% Or and 3.4% Ni), 6002
0,6% 0 and 2 and*129G2 (1.29% C and 2.7% Mn).
For each of those, two te-mperatures (Tl) of preliminary
transformation were seleated and.two temperatures of
subsequent transformation (T2) in the minimum range-
These temperatitres.vere as follows% 405 and 395 001
300 and 260 OG for the steel 53 T = 4,00 and
KA3;
T@O 350 and 300 00 for the stee S2. After
3 00 T2 8
prelim nary trans forma tion at the temperature T- - the
a A.I. carta
subsequent _trans-forLit-40 -- r.----T-J--began--a:ft;a
--Cardl-/4----=diibiti:ii7p'iiiii.od:.--.- in Figs 1-@ the influonoe is

BOV/129-5?-k2/
,J5
Certain -Levi Governing the Transformation o esi ual Austenite
raphed-of the partial transformation of the austenite on
t
he kinatics'of subsequent transformation for the three
tested:steels. ;A drop in@the degree of transfoization
at the temperature -T2 after partial transformation at
the temporature-Ti',was observed for all the investiga-
ted steels irrespective of the sense of the concentration
changes oZo@;ringin the austenite, This drop in:
ticularlY large if thetransformation at-the tempera-
tre TT proceeds until damping occurs. It can be
as sumea ..that. this [e-mail] as self-braking.of. -the
'intermedixLte.tz;ansformaZ/ion-at a constant temperature
-is related to the martensite mechanism of gamma-alpha
transformation in the intermediate range. The kinetics
of transformati,;'@i-.of- he
t -residual-. austenite during
tempering! of." hiidined':st461'c
omply b@Lsical y vith the
same ielationi@ ihiah were established for isothermal-
austenite transformation by Cohen (Ref 11) and by the
authors, of this paper (Ref 12), ThiSLassumption is
confirmed by the transformatiowdiagrams of the primary
and residual austenite of the ste,61 73KhN3 containing
Card2/4 0.73% 01 0-8%.Cri 3.5% Ni (Fig The influence of

SOV@129-59-6-2/15
Certain Lave Ooverning the Transformation of esidual Austenite
'partial intermediate transformation of austanite on
subsequent tranaforMat4on at lower temperatu
res is, one-0
the basic eau0s of the differenas in the kinetiatofi
transformation. of austenite.under isothermal conditional
whidh also--applies to continuous aouling. Behaviour! 16f
the residual austenite, during tempering depenrls to. a i
considerable extent on the conditions of 'hardening of the
steel and on the chemical composition. For evolving
rational heat trziatment, regimes it is also
take Into cons:fdar-ation.the features.of the kinetics-of
trans format ion, of residual austenite during temp6ring,
Preliminary experiments have shown that if steel which
contains a.considerable quantity of residual austenits,
is subjectedto heat treatmentg the impact strength can
bo:oonsiderably improved by do-able tempering. For this-
purpose it is advisable to first:temper the steal.at
temperatures corresponding to the lower part of the
intermediate range arzd.then to Increase the tempering
temperature to.60o - 65o oc. In the ease of direat
..Card3/4

5/129/61/0007/002/oi6
3073/9535.
AUTHORSt Entin, RO I$@,, Doctor of Technical Sciences,Profossor-
and Kogan, L,- 416 6 i, Candidate of Technical Sciences
TITLEr Redistribution of Carbon.During Int*rmediato
Austenite Transformation
FUIODICALs M*talloyodtniye i tormichoskaya obrabotka metallov,
1961, NO-7. PP-7-11
TEXTt, Accordins.to earlier investigations of the' authors,,
the nature of the changes.in the carbon concentration in residual
austenite depends on the chemical composition of the steel-
During transient transformation the carbon concentration i; the
residual austenite becomes highly non-uniform, This follows from
metallographic investigations and from the results of measurements
of the lattice parameter of the residual austenite in the case of
step cooling to temperatures lower than room temperature.
Measured parameters of electrolytically isolated austenite also
indicate that after partial intermediate transformation the
austenite will become non-uniform. Some features of the re-
distribution of carbon in the austenite may escape notice, since
Card 1/6

Redistribution-of Carbon ... S/229/61/000/007/002/oi6
sectiona'af re idual,-austenite.with the lowest carbon concentration,
wh,ich do not Mome transformad'into the *-phase at the isotherm
temperatures,.may become transformed during the cooling.process.
Furthermorel.tht lattici parameter of the residual austenite can
changa,,depending on the fraction of martensits in the structure.
Therefore, the authors considered it advisable to determine the.
lattice parameters of austenite'directly at the intermediate
transformation temperature. In.earlier work such measurements
were made on-steelm--whlch.-after-quenchlng, had An austenitic
structure and for which'the intermediate transformation occurred
on heating to.300-400*Co It was'-found that the lattice parameter
of the austenite:decreases during .the process of transformation.
Comparison of the date of high temperature X-ray exposures with
results measured after cooling the specimens to room temperature
have confirmed earlier established relations and also the
considerable nonuniformity of the carbon distribution in
untransformed austenite*, The authors used a special chamber for
high temperature X-ray exposuresedeveloood by E. Z. Kaminskiy and
Li I. Kogan (one of the authora)gfor direct study of the.
austeni a of various steels during intermediate transformation.
Card 2A

243-88
Redistribution of Carbon ... 5/129/61/000/007/002/016
E073/9535
The compositions of theme stools are given herewith (in
Steel C si Mn Cr Ni MO
(53KhN3S) 0.53 1.22 0.32 1.42 2.35
5.1X3(-,1VM 4.52KM752ram) 0.52 2.18 1.8 2.97 0.38
jrOX4- OOKM) o.81 o.16 0.28 3.86
The selection of the steel compositions were based on the cooling
conditions in the chamber and on the conditions of making the
!X-ray exposures. It was necessary to ensure a high stability.of
the austenite In the pearlitic range so as to prevent pearlitic.
-transformation during cooling and also.a high stability In the
intermediate range so as to permit taking numerous X-ray exposures
during the process of transformation. Specimens 0.8 x 10 x 100 m
were vacuum annealed for 1,0 hours at 1150% and then they were
-etched so as,W-remov* the docarburised layer. Following that
the specimens were heated by passage of an electric curreni to
Card 3/6

Redistribution of Carbon S/129/61/000/007/002/016
2073/2,535
930-950"C in a holium''atmosphere far a@period of 5 min and theW
cooled. to the,isothermal holding-tomperaturt. The temperature
was measured with an accuracy of 5"C by.means of a welded-on.
platinum-platinum thermocouploo The exposures wore made
with the K radiation of manganese and an exposure time of
20 -min focualing onto the (311) line of-the austenitee "It was
found that this interferenceline became strongly blurred after
the beginning of the intermediate transformation (Table 2). Since
type I distortions:were virtually.absent from the 0.8 mm thick
specimens. which -were cooled at a moderate speed, a change in the
position of thecontre of the line during the process of trans-
formation must be associated with a change of the average
concentration of the carbon In'the austenite. In the steel53X 143
(.53KhN3) the average austenits Iparameter increased 14-fold in the
steel 52Kh3S2GM 11-fold corresponding to increases in tne average
carbon'concentraL*ion by 0.3 and 0.25%. respectively. Another
series,of experiments have shown that the width of 'the austenite
line during intermediate transformation is determined to a
considerable extent by the distribution of the carbon in the
Card 4/6

of Carbon' .0/129/61/000/007/002/0 6'

and notby type XI distortions or by refining of the
blocks. Xnvestigation -of the steel 8OKh4 in
the medium
,
temperature range has shown-that::the;lattice pnrameter of the
'austenite does not change during.intbrmediate transformation*

;.The following * conel
usions were arrived att
@1. xt was experimentally confirmed that a pre-requisite of y--)P-A@
-transformation in the intermediate range is
the redistribution ot
,
carbon in the austanite.
2.,Red:Latribution or carbon leads to the formation of areas with
.differing.carbon concentrations. Areas with the lowest carbon
@concentration ensure the possibility of martensitic transformati n
0
.,at intermediate range temperatures. The peculiarities of redistri-MIII
' AI@@'.
bution
of carbon in the austenite depend on the initial carbon
content in the steel and the nature of the alloying.
@,3, Redistribulion of carbon,and presence of areas with changed
Ilattice parameters of the austenito'can be observed only if those
taro relatively stable and.the formation of carbides instopped.
Apparently, in,alloyed as well ai in carbon steels containing
!0.8 to 1%@C, the carbides form sufficiently rapidly so that the
:Ilattice period of untransformed auatenite does not change.
Card 5/6

2,

lRedIstribution of Carbon 5/199/61/000/007/002/oi6, -7

'figures,'. 2 tab Ilea and
Thero are 2 7 references3 all Soviet..
-ASSOCIATXON: TaNIIChM-
-Table 2.
1, Frame.No, L+) 6
2. Time f roin the beginning
I
.
min
of the transformation,
tit
f t
f
d
Q

- l
Ii
uan
rans
orme
3,
y o ie
ft
@
austenite,
4.'-Width of the
011) line MM- Crap 53XH3C, 1130?epma W.
-
1
5. Distanco'between the
lines# rimi
-0-20
0-

10

4
1
604

20,3 J1400 3,
"
-Bragg-ang --40, 10--W

@@78 3.9

-4
0 27 37 -36

Cis- 74W 3*6 13

16

0120
,

R
----Cha n.
inge he,car on
content, CTub 52X3C:2r*, X30TOPOC' 01(1(
@.53KMJSi .:Lao thorra-ax@'-, ijkv,
4 4""
Oct. 0-7 i's :25i5 76V
0
42 ?.@m 3A 26.0
E@
@1-7
7@4
3
r 40 4,0 26
eel @$=h3SWIt
.5
- _
4 W-W 3.6 26
310,0C 's 74040' 3
5 7
n
35 26,6 74VI 3
1 4 3.601@,21
80-200 41
3M-42D 80 3:8 26,9 74-4 .60 2.4
So
Card 6/6
7f
03
4

g65S6 6/126/61/012/002/005/01.9
R073/19333
it-is
AUTHORS: Koganj Lolo and Entin# R*I,.
TITLE: nterwedlate Transformation of Austenite in
Carbon Steel
PERIODICALt .-Fisika metallov i motallovtdoniye, 1961, Vol* 121,
-No. 2, pp, 204- 2017
TEXTs So farl no definit's data are available.on'the upper
temperature of the:range of intermediate transformation in
carbon stools. The causes that determine the features.of
intermediate:trwinformation in carbon steels have alsotjR9t, boon
clarified. The authors investigated the formation of/surface
relief in carbon steel containing Oe9% C by direct microscopic
investigation of.a polished section of the specimen in high-
temperature vacuum equipment* It was assumed that high-
temperature heating and the use of thin (1 mm) speeikens would
make possible undercooling the austenite down to temperatures
of the medium range and observation of the process of formation
of the surface reliefo The specimens were heated for 15 win
Card 1/5

Ijit erm'ediat a Tranof ormatiow:
at I 150'OC and,during this proc*sx..the austenits grain:grov;-
to large dimonsionj (0*5 - 0.6 mm in diameter)* The specimen
was coole&to 540 7C, at,'which temperature it ''was hold for
5 min (until transformation.wax completed),; subsequent-cooling
tp room,temperature did not lead to formation of a reliefs The
test.results indicate that this temperature is in th8 range of
pearlLtic trans format ions ...Cooling from@l 150to 530 C led to
the growth of only a *ery small number of crystals (a few
crystals in each,grain) during the-first 3 seconds after the
ippecimen reached this.temperattire.' Further soak:Lng at this
topperature for 5 min and cooling to room temperature did not
rokult in any additional:reliof formationo- This indicates that---@
partial intermediate transformation in followed directly by
pearlitic transformaSion. If-cooling prooo*ded after holding
the specimen at 536 C for 3 seconds an additibnal relief formed ktl@
at the surface at lower temperatures-of the intermediate rang*
and below the martensitic point-.(230 00. The data obtained
make possible the plott1dLX of an isothermal diagram of the
Card 2/5

Intermediate Trans for:mMaon 2073/2335.
intermediate transformation of -the aunt enit a carbon (0.9%)
steel Fig.L 5 s4ows%the diagram of the isothermal trans-
forma;ion,(-Cl-veraus time in sec.s.and min). The curves of
the beginning and end of the austenite transformation were
determined magnetometrically; the hatched (intermediate
transformation)'area was determined on'the basis of observation
of the relief formationo High-temperature metallographic
investigation of the surfrice relief enabled establishing,tho
range of intermediate transformation in steel containing O@9%',
cwboY3. The upper temperature of this range*is 530 - 540'%OCI
in the temperature range530 - 470 OC intermediate transfor-
-mation develops only to a certain extent and pearlitic-trans-,
formation will occur afterthise The degree of intermediate
transformation Increases Iwith decreasing temperature. Thus.,
it is shown that characteristic features of intermediate
transformation exist in carbon steel, namely - self-braking at
a constant temperature and temperature-dependence of the 11wAt
of transformation. The medium range of transformation could
Card'3/5

S/126/61/012/002/005/019
Intermediate Trans 0 on 9073/E335
not be-detected in 32umerous.earlier investigations due to
the high speed of the process of pearlitic transformation.
which follows intermediate transformation.
Thereare 5 figures and 10 referencest. 8 Soviet and
2 non-Soviet, The 2 English-language references quoted are$
Rot. 6@_ Ko, T. and Cottrell, S*A. - J. Iron and Stool Inst*9,
1952, 172, p. 31 .Rot# A_!@L&azv
a oib-&-t-0ii apanq-@1935, Vol@ It No, 26'
-of "'J
ASSOCXATIONt Institut@metallofiziki ToN1IChM
(Institute of Pbvics dfMetAls , ToNXIChM)
SUBMITTED: Docember-'10,., 1960 (initially)
January 17 196i (after revision)
Card 4/5

S/C,132/61/027/006/015/018
B1241B203
AUTHORSt Kaminakiy, . E@ Z.-. and Lo-g& n I@111 -
TITLEt HrobAngo of experience
PERIODICALt Zavcd6kaya laborLtoriya, vo 27, no. 6, 1961. 761
TEXTs POT studyIng the in -termediate stages in conversional the authors,
improved a high-tomparature' chamber which had been described earlier
(Ref. It E,, Z-@ Ktmirakly and T@ 16 Stelletakaya. Problemy metallo-
ve.deniya i fljzlki mitallcv, 2, 240 (1951)). The aptkciman, i-10-M mml,
was placed in the interspaSs betwqen the water-oooled oopper electro-
des, and electrically htat*dd k transparent fcil :)f 'nep@onbflK-4 (Per'-
foll PK-4' capr-ors. 10@t thick,
it stretched over the chamber window,
tae (iistanco) between ap#eimRn and, film boizg 45 mm, Expaure time is
20 min., Befcre oparafloa,*, tho'chamber is evacuated and then filled
with bell,@ni_ To pxevent bendIng of-tho specimen during heating to high@
temperat-,;rts @@a@ovjt 9000C)t a 5ewthiok nickel foil ;a welded to the
speolmon,- The X-ray patterns showed the ni-ko.) banlq besides those
of th# steel'invw 'Jgatrd, By measuring the of the nickel
band-4 at a ctr-7ain temperature, it wat also pi@ssibI4 to calculate- the
Card 1/2

B/O'5216110271006101510IS
Exchange of tiperionoe B!24@B2031
and film@ Wher heating the specimens to 900100
and @@oclfng to 300. - 2750C. no iron diffuses snto the niokel foil. There
.15 1 S')Vlet-bioc. reference,
ASSOCIATION# Trjentr&l@nyy n&vabno-isetiedov'atel'skly inatitut chernoy
motallurgtt Im. 1. P,.Bardink (.central Soitn'tific Re-
search lnet%tute of Ferrous Metallurgy imeni I. P. Bar-
din)

- -- -- -------- 214%
8/020/61/138/004/010/023
Misto BiOVB203@
AUTHORs x4ant Lo I andEntint HO L
TITLEs studies of carbon concentration in the alpha phase in
intermediate.transformation of austenite
PERIODICALs Akademiya, nauk SSSR-. bokladyt V. 138t no-. 4P 1961
826 627
TEXT .s In the introduotion't the@'auth ore. discuss recent studies stating
that the austenite transformation iri'the medium temperature range con-
sists of a diffusion redistribution of carbon in austenits and a martsn-
site transf ormationf -a . The formation of part of the austenite with
higher carbon content permits the. martensite tranef crmation y-a at sodium
temperatures above the N point [Abstracterte notes N point not defined.)
It was shown that the redistribiltion of carbon is a necessary condition.
t - r the - a u-th o-r-s-- had
--for@the formation.-@and- t
'grow.
shown in a previous -papsk.that the carbon concentration in the a-phase
at the instant of transformation is lower,than the mean carbon concen-
tration in steel (Izv. AN PSSRp OTNv no* 6 (1956))o The method used for
Card 1/4

S@IP.61/138/004/010/02 3
Studies of carbon concentration B104 B203
these studies didp howeverp.not,,allow a determination of the carbon a on-
centration in thea -phase on the transformation temperature-in the medium
range. For this reasong the authors made X-ray studies of the a-phase
directly at the transformation temperature. They studied a low-alloy
carbon steel of the composition 0,23 0 Cl 2.1 % si, 3 % Unt 1.8,0 Nit
1 . 8 % Cr* and 1 , 3 % To The oonoontration of the a qhue was determined
from the width of the (211) interference linso The specimons'were heated
in a chamber directly with oloptrio current to 1150OC9 held at this
temperature for 5 min# and subseq uently cooled down to the temperature
of the isothermal. After the end of the austonite transformation
det8rmined by magnotometrio measurementev. the speoimene-were heated to
300 01 thong. the X-ray piotures were takeno it this temperature, carbon
is not released from the a-phase# and there in no new austgnite trans-
formationj this permitted a comparison of the line widths of the a-pbasee
For determining the carbon concentration in thea-phaso from the width
of the interforeno* linest the authors used a calibration curve plotted
with the aid of studies-of hardened steel with carbon contents of 0.05
0*25 %. Results are gi@,on in Table 10 As can be seen, the (1-phass formed
in an intermediate transformation contains lose carbon than corresponds
Card 2/4

33459
5/129/62/000/001/001/011
'E193/Z383
AUTHORS: Kogan, L.I., Candidate of Technical Sciences and
Entin, Mi., Doctor of Technical Sciences, Professor
TITLE: The effect of detorwation of supercooled austenite
on properties of hardened steels
PERIODICAL: I Metallovedeniye i termichoskaya obrabatka metallov,
no. 1, 1962, 3 -_9
TEXT: A new method of improving the mechanical properties.
of steel has been developed in recent years (L.V. Smirnov,
YceN. Sokolov and V.D. Sadovskiy - Trudy instituta fiziki
metallov, no. 18, 1956.. Refs 3; E.M. Lips, H.V. Zuilen
"Motall ProgresSI!, V*66,,no. 2, 1954 s Refs 4), which consists
of plastic deformation of supercooled austenite followed by
conventional hardening and tempering treatment, and to which
the term "TD1011 (abbreviation of "termomekhanicheslfaya obrabotka")
has been'ascribed in the Soviet Union.. The main objuct of the
present investigation was to study the effect of this treatment
on the mechanical prope 'rties of steel 4oxR50 (40KhN5S) which
was chosen for this purpose because its austefiite remained stable
Card

)3459
S/12j/62/o oo/ooi /ooi/oiI
The effect of deformation E193/F,383
0 @O
at relatively low temperatures (570'- 50 C
The
composition-,:-
of this and-other-steels used by the present a uthors is given
in Table 1, as follows:

Melt Type of steel Composition,
No. C Si Mn Cr Ni
.4ox H 5c (4oKhN5S) o.41' 1.'39 o.o8 1.65 '4-54
2
40KhN5S
o.4o 1.4
0.07
1.65 4*53
ICX
3 42)(I.GCKI (42KhN5SMP)
o.42 1.85
0.25
1.86 4.15
4x 31XI4 5C (3:LKhN5S) 0.31 1.45 0.07 1.45 4645
X
5 33X 4 (33KhN&5S)
0-33 1.35
M4
i.6o 4.20
x denotes vacuum-meltIng
.xx means that the melt contained 0,48% Mo and 0 .25% V-
Card 2

33459
S/129/62/000/001/001/011
-The effect,of deformation Z193/E383
In the first series, of experiments the effect of both
conventional treatment and TMO,on vacuum-me1ted steel 4OKhN5S
(Melt 1) was studied. The conventional treatment consisted of
oil-quenching the steel from 850 OC-and tempering it for one
hour at various temperatures. TMO was carried out in the
Tollowing Manner: @he test piece was heated in a furnace or in'
a salt bath to 850 P, after which 0it was transferred to a
molten tin bath maintained at 525 C-. After it had cooled.to
525 OC the test piec,e was deformed to 70% reduction with one,
or two strokes of a drop hammer; it was then immediately oil-
or water-quenched, afterwhi,ch.it was temper8d for one hour
at various temperatures between 200 and 650 C (in some cases,
rolling instead of forging was used to deform the austenite).
The.results of these-tezts (carried out on test pieces I mm
in diameter) are reproduced in Fig.-2, where the yield strength
2
(e , kg/mm graph a) and UTS (cob, ks/mm graph 15) of steel
S
4OKhN5S are plotted against the tempering temperature the
circles (1) and dots (2) relating to speciments treated by the
conventional and TMO methods, respectively. It will be seen
Card

33459
5/129/62/000/001/001/011
The effect of deformation @E193/Z383
that a maximum increase in yield strength and UTS of steel
subjected-to TDJO was attained in specimens tempered at 220 C&.
Und6r these conditions, 260 Ra/mm 2 and 330 kg/Mm 2
Ole
Were occasionally attained; in these cases, elongation and
reduction of area were, respectively, 5 - 6 and 30 - 35%. The
hardness of steel 4OKhN5P, after,TMO but before tempering, was
HRC 599 i-e. 3 units higher than that of the same steel hardened
by the@conventional method.. The improvement brought about*by
TMO, when applied to steel 4OXh145S, melted in air, was less
pronounced; this is shown by data reproduced in Table 2. To
check -the effect of size,of the test piece on the results of the
process studied! :tensile spedimenst 3 mm. in diameter, Were used
in the next series of experiments. The results are given in -
Table 3. The effects of other variants of TMO on the properties
of steel OKhN5S (malt 1) are shown in Table Some significant
results were obtained When TMO was applied to steel 42KhN5SMF
(melt 3), in which secondary hardness@ia developed during
tempering at 450 525 _oC. It was found that high mechanical
C ar d 4 lkj:;

The effect of deformation
33459
S/129/62/000/001/00]L/Oll
E193/E383
2 2
properties (cprb 200 210 ks/mm Igo US/= ) imparted
to this stool bx TMO were retained after tompering at temperatures
as high as 500 C#' The results of'the next series of experiments
confinnedthat TMO brotW*.about a decrease in the size of the
martensite grains. It was also established that this effect played
an insignificant-part in the increase in strength brought by TMO
that there was practically no difference between -the block
dimensions and the magnitude'of stresses of the second type in
specimens subjected",to the conventional and TMO treatments, In
the next series of oxperimentst carried out on steels 31KhN5S
and 33KhN5S,it was established that the beneficial effect of
TMO increased with incroajing degree of plastic deformation and
that deformation at 525 OC biaght about an Increase in strength
of the austenite. The effect of the carbon content in this
-st'eel on the effectiveness of TMO was also studied. It was found
that whereas the increase in strength brought about by the
application of T),10 to an 0.05% C steel amounted to 10%, the
corresponding figures'for the 0.14 and 0.24% C steels were 19 and
210.0, respectively.. It was established also that with increasing
Card 5

33459
The affuct of dofo 9193/9383
W,
Ccontent of the austenite,.its rate of work-hardening increased.
This effect is illustrated in Fig. 4, showing stress
0', kg/mm2) versus strain- (C diagrams for austenite in
steels containing 0.05, OA4 and 0.240% C (Curves 1-3, respectively)
tested at 525 0C. it is stated in the concludIng remarks that the
relatively greater improvement in the mechanical &operties of
vacuum-melted steels subjected to TMO is associated with their
high purity and the resultant high plasticity of both austenitie
and martensitle structures in which, therefore, local stress
concentrations leading to the formation of microcracks are less
likely to arise. There are 4 figures. 8 tables and 8 referencesi
6 Soviet-bloc and 2 non-Soviet-bloc.
ASSOCIATION- TsNIIChM
Card 6Z

--------------------------------------
5/126/62/023/005/021/631:2.
Elll/E435
AUTHORS: Drosdo 8,Y&,, Kogan. L&.I,, Entin, R.I@
'o
_TITLE: Influence of'stress-And deformation on the kin i f
et CS
the-intermadia.te..transformation of &ustenite,
PERIODICALs Fizikti, met-a-Ilov'A. motallovedeniye, V,131 no,5,@1962t
176-779
TEXT., Information on thi:ekf*ci-'of--d*form&t1*n,of metasta'ble.
au3tenite.followed by,quenching bn:the austenite transftrmatlon@l,-
incomplete. -Theauthors-@have studied the kinetics of the
transformatiowunder pplied-load'conditions on type 40x H5C
(4OKhK5S) and 80X4 (80Kh4) ate's-18`0 For the ffrat, loading was
carriedout at 6.6-mm/isin-to the required stress whi;mh was then
kept constant wi*thin,+-! ki/mm2, The kineticswere studied at
300 and"350"C. , Acceleration occurred at all@the temper&tures,
being sapeciall~r.markod-&-t'tomporaturoo of the lower part ofthe
intermediate region.- -The'@-influ*nce of rate of deformation was
studied at 3001' 4O0and::S25*C* this and other work shows that.
when conditions for thernoxechanical treatment of stools are
Card 1/2

...........

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71 @ IM 11 f ''.
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.. 1. @@ I . , , I . -
- . I I, I r@, 1 ,
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; . I I : - , !I I . I.
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L )JWA(d)/T-/EWP(t)----1J
--I M-.66 EWT(m)IEWPLw P(a)---JD
-ACC NRs AP6012234 UR/0129/66/000/004/0019/00X
SOURCE CODE.,
-AUTHOR: Baihchenko, A..-Es; Gureirich, Ys. .-B XoMn. L. I.; Taymer, D. A.;:, Entlas
Ro 1.
ORO: TsV1I
:TITLE: Investigation of steels,,i-susceptiole to-secondary
ened
SOURCM Metallovedenlye termitheskays obrabo;tka sitallov# no@ 4, 1966 19-21:
TOPIC TAGS: -is teal treatment, thersomechanital, treatment,.Iow.tesper&Ctica~tre'statat~*
-42
high tesperatiiira-trestment-~/4SKhSM3F, MINUFS, 44Kh5KVFS. 6OKhSHM
STRACT: e effect of 11inK40chanical treatment an the properties of 45Kh5M3F0._
k
B2Kh2N2VFS,k4Kh3MVF8, andMOOSIMS structural' steels susceptible to secondaty/
hardening has 3een 16eatliste& temperature-thermomechanical treatment 0
(austenitizing at 1050-IIOOC-for-15- 20 min# cooling to 550C. plastic deform-lion
,with 75% reductiop, water quenching followed by refrigeration in liquid nitrogen and
tampering), impro d the strength of all steels tested. For instance, at 330C the
tensile Atmingthl" 230@-266 kS/wm2._ the yield stroagth@ 233-.260 kit/=2% Ahe
elongation - -ja, an4 the redUCtigg of area 15- 302., Corresponding f I ures for 480C Ven
204- 246 kg/=@2 9 104- 236 *g/= . 3--4; and 18--38X. However,, 42 ': '52M and 60&"l
_N_ thi a '_'Wjjj;nja -or @texp
ered,conditian weie1rittAt room4eimperature
_The.yield iqrength can be'locreased to about 200 kg/=2 at 500C and about 2
50 kg/mn@
6rd lL2 Jwt 119.374i621,761

N -2
ACC NRs AR6013665 SOURCE CODES UR/0058/65/000/OliF/CO207 8
AUTHOR:
L
Entins R" Is
TITLES The transformation of austanito In the intermediate region
SOURd: Ref. zhe Fizika,.Abs. lOE219
rxr SOURCE: Sb. tr. In-t metalloved. I fiz. votalloy Teentro no-i. In-ta chernoy
metallurgii, vyp. 36, 19640 222-226.,-
TOPIC TAGS: crystal growths austenits transfomation,'(steel U9 steel, 100 M stools
9OS2 steel, 70N3 steel.
TRANSLATION: The growth.rate of a-phase crystals during intemediate transformations
(at 250, 300-and 35000 was measured in U99 100 No 9OS2 and 7ON3 steels on the LOdn"
9kLy apparatus. It Is hypothesized that the growth of *-phase crystals is limited
by the rate at which C Is removed from the edge of the growing crystal. The small ac-
tivation energy of and Intermediato transformation (12.,000-14,500 cal/giam-atom) AS
compared to the activation on .orgy for C diffusion in austanite.(32,000 cal/grm-atom)
is related to the high stress that occur in sustenite during a transformation and only
slightly relax at intermediate tow4peratures. The effect of alloy elements an the
growth rate of a-phass, crystals- Is discussed* .9 references, Is Tulupova.
SUB CODES U,20
cam

jmu,,-j.X, IONATOVA N.f

/62/060/01.2/001/009
D201/D308
413THOR:
a
TITLE: Design of fdrromapetic' probes
PERIODICAL: Priborostroyeniye, no. 12, i962, 6-8
TEXT: The author considers the problems met in designing
axial excitation ferromagnetic probes. *The following concl, ions
may be-made from the analysis of the induced omf spectrum: 1) the
amplitude of the excitation field,.which results in the maximum
am. l'itude of a given harmonic increases idth the order of this
harmonic;'2) the excitation field amplitudes, corresponding to the
maximum am litudea of odd.harmonics, are simple ratios to those of
even harmonics; 3) the.ratio of even harmonics amplitudes is direct!;'.
ly proportional-to the amplitu4e'of the excitation field. Afte'r
selecting the.core material it is necessary to find the incrementaf
eability of the dore shape. A formula for the probe sensitivity q
perm
G is given. Sevdral probes, designed,'according to the above princj.-'
ples..havb [e-mail]'on the average by I to 670
from theoretical values. There are 8 figures,
Card 1/1

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