SCIENTIFIC ABSTRACT ROZENBERG, V. M. - ROZENBERG, V. R.

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• Collection: Scientific Abstracts
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• Sequence Number: 13
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

SOV/126-6-2-19/34
Study of the Influence of Preliminary Deformation in the Cold.
State on Creep
inter-atomic bonds in the crystal lattice.' Thereby, it
is necessary to take'into consideration that conservation
of a structure which ensures a high strength at elevated.:
temperaturns also depends on the strength of the inter-
atomic bonds. The creep speed of specimens hardenea.by
deformation in the cold state and notpreliminarily
stabilised increases sharply in the temperature range
where recrystallisation occurs. Thereby, the stage:.
with a steady state creep speed shifts towards longer:
time durations, Under@the simultaneous effects of
temDerature and stresses, softening of preliminarily,.
deformed specimens it more intensive than solely as a
result of elevated temperatures. There are 5 figures,
4 tables -Tid 6 references, 3 of which are Soviet, 3 English.
ASSOCIATION: TsNIIcheriaet
SUBMITTED: December 17, 1956
Card 3/3 i. Ailoys--D,eformation 2. Alloys--Creep 3. Alloys--
Heat treatment 4. Alloys--Test results

SOV/126-16-4,:;-32/34
AUTHORS; Rozenberg, V. M. and Gradova, L. V
TITLE: Phenomena Associated with Grain Boundaries.in the Case
of High Temperature Deformation of a Solid''Solutionof
Titanium in Kickel,(Yavleniya, sv-yazannyye s I1@ranitsa,mi
zeren pri vysokot6mperaturnoy deformatsii tverdogo,
rastvora titana v nikele)
PERIODICAL: Fizika Metallov i Dle-tallovedeniye, 1958, Vol 6.: Nr 4-
pp 765-767,(USSR)
@ABSTRACT: Data are givPn,relating to the displacement of, grai -n.
boundaries in solid solutions of titanium
containinp- 3.60% Ti. :The stretcqng of the specimens was
effected in vacuum at 900 C after preliminary.,
or
annealing at 12060C for 2 to 3 hours. The micro-structure-
-c-he dis @th
photos Figs 1 and 2., show place@ent of e ;zrain
boundary in a sRecimen stretched at 700.0 by means of'a
load of 8 k&/mm,--. The displacement of the bent boundarv
on which the observations were carried out,took place
in the direction away from the cent're.of,curvature, This
seems to indicate that the moving force of the displace-
ment is not the difference in the magni-mde,of the surfa
Card 1/4 energy of the@gra
ins but the difference in the elastic

SOV/126-6-l'-':12/34
7 J
Phenomena Associated with Grain Boundaries,in the Case a 4i-In
Temperature Deformation of a Solid Solution of Titanium in
Nickel
energy of each of the grains, Fig 3 shows the case.of
displacement of boundaries which is accompanied by @hel
formation of @liding lines in the specimen,(Ni, 600 C,@
cy = 3.5 kg/mm ). At a higher test temperature. the .
-displace'ment of boLuidaries can be. so, large that in,
individual cases it is a grad al
possible to observe, u
cessation of the grain. It canbe seen from Fig.4.
how an initially large grain is gradually "eaten up". by
its neighbours. The photographs depict individual'
stages of thedisplacement. It can be.seen clearly that
this takes place with breaks: each break corresponds,,
-to a certain position ofthe boundary. :The,observed
change in the structure can also be explained Dy-.the
displacement of the grains relative toeach other.:.Such
a displacement should bring about a buckling of individual
grains which, under the microscope,can be seen as the.,
Orowth of one grain at theexpense of another (this was
pointed out by E. S. Yakovleva). Three photographs are
Card 2/4 reproduced in:Fig 4 and it can be, stated that the ,

SOV/126- 6-4-32/34
Phenomena Associated with Grain Boundaries in the Case of@:High,
Temperature Deformation 'of a Solid Solution of Titanium in
Nickel
observed picture is due mainly to the growth of.one,
grain at the expense of the other and not to buckling.
This view seems to be supported by the conservation of
traces of original boundaries at 'he individual stages
of growth and also by the possibility of simultaneous
focussing of all grains durin@@ observation with a
microscope and a maSnification of 200 times. It is.known.
that the grain growth in the case of selectilye
recrystallisation is stimulated by the difference, between
the starface energies of -the conjuc@-ate grains, Selective
rk.-irystallis.ation can take -olace at a sufficiently high,
temperature when the mobility of the atoms becomes high
enouF)- Since on the one hand, prior to applying 01
tens@,Ie stresses, the specimens were annealed at,1200 C
and on the other hand, cases were observed@of displace-
ment of the boundaries which lead to an increase in the
grain surface, the assu@iptlon can be expressed thatin
Card _3/1+ the here described cases the state of minimum free.energy

S0V/l2c---6-4-q2/34:
Phenomena Associated with Grain Boundaries,in the Case of HiFh
Temperature Deformation of a Solid Solution of Titanium in
Nickel
to which the system tends during stretching is not baser@
on achieving the mininum surface-energy but on
redistributing the elastic energy between the grains.
The total magnitude ofthe elastic energy is determined.
by the magnitude of the applied stress.
There are 4 figures.
(Note: This is acomplete translation except for the
introductory paragraph)
ASSOCIATION: Institut metallovedeniya i fiziki uie-111-allov TsNIIChM
(Institute of Eetal@og;-?aphy and Metal Physics
TsNIIChg)
SUFvIITTED: May 7, 1957
Card 4/4

SOV/126-6-6'11/25
AUTHORS: Kaminskiy, E.Z. and RozenbeTgi V.M.__
TITILE . Study of the Influence of Dissolved Carbonon the
Re^rystalli2ation and the Long--duration Strength of an
3 '
Ir@l--Nickell Manganese Solid Solution (Izue_-heniye.v1iyaniya
rasivorannogo uglereda na rekristallizatsiyu _J dlitp.12nuyu
pro,-ahnost! zhelezonikellmargantsevogo tverdogc rastvora)
PERIODICAL: Fizika Metalloir i Metallovedeniye, 1958., Vol_6@
Nr 6, pp 1036 - 1039 (USSR)
AB15TRACT. In th-,_ work dese--ribed in this pap r, the authors determined
e
the temperature cf the beginning of recrystallisation And
they investigated the dependence of the long-duration
strength of nickel--manganese steels on the concentrat-io'n
of the dissolved carbon., the temperature and the st-Tesses.
In the'i _n--restigated steels, the carbon was' in Ithe dissolved
stalle and not in the form of carbides. All the investigated
steels were austan-J.-tic and their compositions were as
follows:
Cardl/3

SOV/126-6-6-11/25
."Study of the Influence of Dissolved Carbon on theRecrystallisationt
and the Long-duration Strength of an Iron-Nickel-Manganese Solid
solution
Melt 0 Mn Ni Fe Heat Treat- Grain size,
Nr % % % % ment after ball
forging
588 0. 05 8-? 15-03 nst 1125 0C-2- 5hrs 6-5
589 0.4? 9-5 1---00 " 1100 0C-:-2 6-5
3450 0.95 10 1..@.00 " 1100 C-1-5 6"5
To exclude the influence of the grain size, each series
of specimens was siabjected to a.heat treatment suchthat
the grain size was the same in all.cases (see,table above).
To eliminate.oxidation, specimens were tested in,
argon atmosphere. The in-itial crystallisation temperature.
was determined by the X-ray method after deformation of
the specimens by W16. In Figure 1, the deDendence is
graphed of the temPeratuxe of the initia 'l.crystallisation,
of steels, on the 'concentration,of carbon in the solid
solution. In Figure 2. the dependence is grqhed of the
long-duration strength of steels onthe concentration of
carbon in the solid solution and on the test.temperature.

SOV/126-6-6-11/25
.Study of the Influ' so-red-Carbon on the Recrystallisation
ence of Dis
and the Long-duration Strength of an Iron-N-ickel-Manganese,Solid
Solution
In. Figure 3, the dependence is graphed of the long-duration
strength of one steel on the test temperature. The
following conclusions are arrived at.@ 1) latroduction of
carbon into =on-nicke-31-manganese- solid solution reduces,
the initial reary5tallisation temperature and thus indicates
that the dissolved. -:.arbon ::@educes the resistance of the
solid solution to the effe--ts of the temperatureg 2) the
carbon dissolved in the solid solution brings about a-n
increase in the breaking strength -a-Ii.relatively high defor-
mation speeds and a deicrease in the strength at relatively.
low deformation speedst the higher the 'lest temperatuxe, the
higher will be the def6rmation speeds at which the advantages.
of the -c@arbon-free solid solution will manifest themselves;
3) the here described influence of the carbon i's apparently-
due to,a d - -
e rease in the strength of the interatomic bonds
and an increase in the distortion of thelattice of the
solid solution. There are 3 figures, 11 table and 11, Soviet
raferencis.-
ASSOCIATIO TsN IChM
D May 6. 195?

18(7) PWR I BOOK EXPLOITATION SOV/3355
Akademlya nauk 533R. Inatitut,m Ietallurgil. Haucbnyy *over
o,
p
prablem* zharoprochnykh apl&vov
1smlftdOvAnIYa PO zharoprochnym aplav&m. t.
IV (Studies on Heat-r,-
xistant A.1joys, Vol, 4), Moscow, lzd_vo
AN SSSR
1959
400
.
,
p,
Irr'Lt& slip insert ad. 2,200 copies printed.
z>
Ed. of Publishing House: V. A. Klimov; Tech. Ed. . A. P. Gu3eva;
Zd1tDrLAl -Board: 1. P. Brdln, Academtclan; 0. V. Kurdyumov /V
,
Atad"Iclan; X. V, Aseyev; corresponding Member, U=SIR Academy of
L
Sciences; I an
I. A. Odin&, 1. 14. Fav ov, d 1. P. Zudln, Candidate
or, Technical Sciences.
PUN?= ; Th is book is intended for 0011, Ilurglata concerned with
''the structural metallurzy of alloys,
COVEUCIR: This IN it collection. 0f specialized studies or various
problems in the structural metallurgy of heat-re3letant alloys.
Some ar& concerned with theoretical principles, now, With dnj.
crIptions of new equipment and methods, others with p.-opertlea

peciflad conditions are studied and reported on, For datftils,
*a Table of, Contents. r The articl,63 are sccoopml4d by a num-
:
ber or ref4rended. both Soviet and non-Savlet.
TABLE OF CONTENTS t
3av/3355@
UU41,49 (Cont.)
and v. I., syutkina. mechanism Of High
V`,k-_1-W3.,-Z-.-S
kel-
d Ni
c
an
Temperature
Copper Solid. Solutions
QbAtk1ru_ and
ans format ions
A 3tudy or 3tructural Tr
nyo
xwrop
41
In Rs&t_ -Aluminum A11074
,
:
.rqsi tan opper
and V. P. SukhovarOv. Con

;. V
of e c5nWekkanlng
Efr
ee
ceraiO4 t Stimuzating
h
In D#fOrEWtIO83
onahlp Betv..n D.ror%atlon In the
I
reep
1~11 During
ant along tho Bound&-
in Nickel
on the Equivalence of thd Effect of Rate and
64
10
Of Plastic Plow
_
-qemparnture f 3train on the rrocess
V.,3_RIkhAl6nkOV`, and R. 0. PAdfttOVM-
Detntyar
Card 3/12.
K_

sov/18o-59-2-9/34
AUT-HORS: Minkina Ye A Preobrazhenskaya, N.V., and-RozenbergV.M.
(MOSCOW3
TITLE: Study of the Deformation of Nickel During Creep
(Izucheniye deformatsii nikelya pri polzuchesti)
PERIODICAL: Izvestiya Akademii Nauk SSSR, Otdeleniye tekhniches-kildh
nauk, Metallurgiya i t6plivo, 1959,Nr 2, pp 48-55.(USSR)
ABSTRACT: V.M. Rozenberg and L.V. Gradova (Ref,l) and.
V.M. Rozenberg (Ref 2) have previously sho,@m that the
effects found to occur in metals.and alloys during creep
are applicable to the particular case of nickel..'Inthe
present work the def ormation of grains, and .,that . due , to I.
relative displacement of grains were investigated. The
nickel used contained 0.02% C) 0.04% Mn, 0.006% S7
0.006% P7 0.08% Tij 0 .23% Fe and traces of Al,and Co. I
Qualitative estimates of.deformationwere made by,the
method of McLean (Refs 3M. Extension of,flat test,,
pieces with surfaces prepared for observation was carried
out in a vacuum installation (10-3 mm Hg). The measured-
values of displacement along slip planes 9nd grain
boundaries and the number of slip lines and grain
Card 1/3 boundaries are tabulated, together with calculated values

sov/18o-59-2-9/3)+
Study of the Deformation of Nickel Dur-ing.Creep.
of the deformation. The measurements werecarried out
at 400, 6oo, 675, 700 and 800 OC7 with stress values.of
13 - 2 kg/mm2. @Figs 1, 2 and 3 showtheaverage valueof
displacement along visible slip planes, number of slip
lines and value of displacement along grain boundaries7
respectively, as functions of time (hours) for 40.0 and
800 OC and stresses of 13 and 4 k /mm2 respectively, are
shown in Fig 4. From the slope oi the line (Fig -5) of.
logarithm of time to attain a,given displacement value
versus reciprocal of absolute temperature an activation
energy for inter-grain displacement for 600 to 800 OC
and a stress of 4 kg/mm2 of 36 k.cal/mol was calculated-,
Figs 6 and 7 show families of curves, for,400 and 800 OC,
respectively, of total elongation and those due to slip
within grains and at,grain boundaries vs. time for@
various stresses. Fig 8 shows the difference between
the total deformation and that accountable to these two
effects related to total deformation as functions of.
time for 400 and 860 OC.. The relation between displace-
Card 2/3 ment along grain boundaries and grain deformation for
these two temperatures and various stresses is shown in_

sov/18o-59-2-9/3L@
,Study of the Deformation of Nickel During Creep
Fig 9 to be linear.. Figs 10 and 11 show photomi.crographs
of the nickel deformed under various conditions. 11 The @@:
work showed that in the first stage of creep.,deformation
of grains on account of visible slip lines takes pla*ce by
way of increasing displacement along slip planes and
-age
multiplication of these planesi in the second st
multiplication of slip lines is the main factor.
Deformation due to grain-boundary displacement occurs
throughout the creep time and plays an increasing, part at
higher temperatures and lower stresses. Certain
boundaries can, depending on conditions7 either hinder-or
stimulate deformation in grains. In addition to displace-,
ment processes associated with slip lines visible under a
microscope and with grain boundaries7. displacementloccurs
through microscopically invisible slip lines and crack
Card 3/3 formation. There are 11 figures) 1 table and'16 references:
5 of which are Soviet and 11 English.
SUBMITTED: December 6, 1958

SOV/126- - -7-5-15/213
-AUTHORS: Rozonborg,.V1.M6 and Gradovav@L.N.
TITLE: Changes in.the Struoturo.of Nickel and Solid Solutions of
Titani um in'KickelDuring High Temperature Deformation
(Izmeneniye struktury nikelya i,tvardykh rastTorOT titana
nikele pri,vysokotemperaturnoy,deformataii),
PERIODICAL: Fizika matallov i metallOlTedeniye, Vol 7, Xr 5, pp 722-731
(+ 1 plate) (USSR) ills-?
ABSTRACT: Th thLs paper the natureof structural changes in nickel and
solid.solution.8 of titanium in nickel during deformation at,
high temperatures (1700 and .@90000) @Were studied.. @@.Tho
composition*ofthe materials studied-is Ahown in.@Table 1.:
In order to obtain uniform grain size of 092-Oo3.mm
alloys wQro@initially annealed, at .1200OG Athe allo7 no,
134 for 1@hour, no.136 for 2 hours and no.137:for@3 Aoiira)o
Theload was selooted so. that 'fracture should occur 'after a,
few t9na of hours. That,deformation at which failure ooevorad
after a few hours.is called rapid,.and that at which it
o caurred., af ter. a f o.w tons,,of hours slow. ..The apoeimens were
..C.a 'Pulled in, a vacuum apparatus. . In Table 2 the,oonditions
rd under,which the specimens wore pulled, and the a is santiia,
W5 test resultal..are shown. The nickel spa eimen no.. 134-.1

Changes in the Structure of Nickel and Solid Solutions.of:Ti,tanium in,
'Nickel During High Temperature Deformation
(the temperature forpulling was 7000C, -stress 5.2 k9/GM12)
can be considered as an example which shows.thechangesin
microstructursoccurring under the action of stresses which
lead to rapid fracture. In Figs.l.and 2 photomicrographs
taken at various stages.of,straining of the specimens are
shown. FigQ3 shows the structure in the vicinity of_the,
fracture. The specimens were also studied by X-rays. .. In
all eases a few sharp points are so Lan in the X-ray photograph
taken of anlundeformed specimen "(see Fig.4). In Fig.5 a
series of X-ray @photographs is shown., taken of the same, point
of the specimen at various stages of expansion. A similar
change in microstructure,and X-ray picture obtained for.,,.
specimen no.134-1 was al8o observed for specimen,no.154-2
(pulling temperature 700 Cp.stress, 3.5 kg/mm2) no.130.o2
(70000, 8 kg/mm2) and no.137-2 (7000C, 6 k /m;@). In the
deformation under the influence of stress which leads to,
fracture,after a few.tens of hours, the change of micro-_
Card structureldiffers from-the above ohanges,andis,notieeably
2/5 independe ,nt of the p.ulling,temper.atur es .used in the experimentso

7-5-15/25
Changes in the Structure of Nickel and Solid Solutions of Titanium 'in
*Nickel During High Tomperature'Deformation.
As an example, the deformation of spa 0imen, no 137-J5
(Ni + 603% Ti) at 90000 and stress of 2 kg/mm:4 is
discussed. In Figs.6, 7@ and 8 the microstructure of a
specimen aft'-er a 4%,deformation and fracture is.shown.
Sub-grains appear not only in grains in whichintense slippage
has occurred butlalso in those in'which only barely notiegabla
signs of slip are evident. - When the,,sub-grains are noticeable
in the slip "lines it can be seen that-there is al:definlto Pon-
ma,tion between the direction of the slip:linea and thalsub-
grains: the long side qf.the,latteris. perpendicular to the
slip lines (see Figs.9@9 10 and 11). In. slow def ormatiou.
the@appearance-of X-ray.photographs taken of the specimions
also changes. in FIS.12:portions.of X-ray photographs taken
of the 'specimen no.137-6 are shown. .@The changes in.atruoture
described for 'specimen no.137-5,, tested at 90000 at a streas
of 2 kg/=2@@are also observed for nickel. @ (90000 alid 2 ke/=2)
Card and for nickel contain Lng 3.6% T-1 .(9000C, 2 kW=@;,' TOOuc,
3/5 g/mm2). In Fig. 13 a photomicrograph of the specimea no.135-7
4

SOV112-6 r? 1512 1@
'Changes in the Structure of.Nickel and Solid Solutions of Titanium in
Nickel During High Temperature Deformation
(nickel 3.6% TI) after straining by 9.5% is shown,:
This specimen was deformed at 7000C at a stress of.139,9
kg/mm2. At 700 and 9000C fracture of the specimen occlarred'
along the grain boundaries at all stresses. As a result of
the above investigations the authors have arrived at th4l,
following conclusionag
1. In the deformation of nickel and solid solutions of,
titanium in.nickel at high temperature4 formation of slip
planes, fragmentation of grains.and displacement of grains-
relative to each other can be Iobserved.,.
2. The fragmentation of grains in slow deformation at high,
temperatures does not appear to be-the primary direet'breaking
down process of the original grain. It is'associated with
the preliminary non-uniform deformation of the latte--j. leading
to lopalbending of,the crystal.. The observable fragmentation
is a partioular.cass of polygonization occurring under the
simultaneous action of temperature and deformation. _Ia the
Card r.egion 700-9000C the possibility offragmentation is deter-
mined essentially by the rate [e-mail].

0-ov/126.. -- 7-5-15/2r;
Changes in the Structure of Nicke.'1 and Solid Solutions of Titanium in
Nickel During High Temperature Deformation
3. In the propeas of alloying nickel with titant-am, fra,#ent-
ation of t-he grains oocura,at- lower deformation ratea than in
pure nickel.
4. The fraeture of specimens tro3ted at 700.and qoCpc 4,31,
Card inter cryst all i-ne in.nature..
5/5 There are 14.figures, 2 tables and 15 references, of wh..
4 are Soviet, ]LO English and I Swiss
Institut metallo,redeniya fiziki metalloy.. T,51i'llChM
(Institute of Metallurgy and Physics of Metals TsNIIOhM)'.@
SUBMITTED-, Jaauar7 20,.11958

sov/v6-8-2-24/26
,m
AUTHORS. Neymark, V.Ye. and Rozenberg,
TITLE: Influence of Boron on Recrystallizati-on of Silicon iron
PERIODICAL: Fizika metallov 1 metallovedeniye, 1959, Vol 8, Nr 211
PP 3,14 - 316 (USSR)
ABSTRACT: The authors have studied the.influence of boron on the
kinetics of therecrystallIzation of an'iron-silicon
alloy with 39'a S!, 0-030% C, 0.2% Mn, 0.0190' P and 0,
0-003t 0-005 or 0.015'a B. X-ray methods were used,to
investigate the cold-rolled (600' reduction) metal.
/0
Figure 1 shows the relation,betweeii.tempera.ture and time
for the start of recrystallization; the,dependence of
the-data on boron concentration is.shown inFigure 2...
The activation energy-rises. continuously with-increasing,
boron concentration. For the.0.01% B alloy the.
activation energy rises with decreasing temperature
ofthe start of recrystallizatiow an effect similar
to one observed by Rozenberg.with,E.Z. Kaminskly (Ref 2)@
and the authors suggest that this should be studied
Cardl/2 further.

18M
SOV/32 25- -?3/51
'A rJT'40R Rozenberg, V. M.
TITLE: Evaluation of,the Contribution of Grain Boundaries in the
General Deformation on Creeping (Otsenka vklada granits zeren
v obshchuyu deformatsiyu pri polzuchesti)
PEPIC)DICAL, Zavodskaya Laboratoriya, 1959, Vol 25, Nr 1,
pp 53 57 (USSR)
BSTP ACT Slow deformations taking place at high temperatures effect
a grain displacement (with respect to one another). Temper-
ature increase and decrease in stress usually bring about..
an increasein the relative deformation share with respect
to,the grain boundaries-The formation of a lattice@j,by
abrasion) permits a quantitative evaluation of the,deformation.
in connection with the grain boundaries (Ref 1). On the basis@
of a schematic representation of a micro.structure with
division lines (Fig 1) the deformation determinationis-ex-
plained and the respectivecalculations are.:given.Jt.is-
stated that the method has a few deficiencies;and,is,also
C ard1/2' inaccurate., To ovoid these disadvantages the fact, is made

Evaluation of the Contribution of Grain.Boundaries in SOIV/32J,25-1-23/51
General Deformation on Creeping
use of that the grains do not displace only lengthwije. A
schematic representation show!@-(Fig,4) that the.vactor of..
displacement can be divided into three components. Two of
them are or the plane- of the saMDle surface.and the third
one is perpendicular with recnect to the plane. The size of
the vertical component can be measdred by an interferoneter
according to Linnik (Ref 4), by the displacement of the
interference waves at the' grain boundaries. Vertical displace-
ments of the magnitude of 0.03-0-05 p can thus* be determined
'bration lattices. Calculation
without the formation of calL
examples, as well as a diagram of nickel creepin, at 8000 and
of-a stress of 2 kg/mm2 (Fig 7) are given. A microscope of
the 'e.TII-4 type was'used. There are 7 figures and 6 references,
3 of which are Soviet.
ASSOCIATION: Tsen-tralfnyy nauchno-issledovatellskiy institut chernoy
metallurgii (Central Scientific Research Institute of Ferrous,
Metallurgy)
Card 2/2

24(2) SOV/55-67-4-3/7
MIMS: 17adgorriyy,. E. M., Osiplyan,,Yu. A.,Perkas M. D., @Rozenber&
T_(TLE: Thread-shaped Crystals With a Strength That Is Near Theoretical
Strength (Nitevidnyye kristally s prochnostlyu, blizkoy k
teoreticheskoy)
PERIODICAL: Uspekhi fizicheskikh nauk, 1959, Vol 67, Kr 4, pp 625-662
(USSR)
@'IBSTRACT: The present paper gives a survey of results obtained (especial-
ly by papers published in.',Vesternperiodicals) concernin.-
the properties and the growth of the so-called "whiskers",
i.e. thread-shape crys-talsq whichg as regards order of
magnitude, are 101 times as long as thick. The strength of
these crystals surpasse's that of ordinary crystals of the
same substance by 10 to 100 times their amount and.attains
values that are near those calculated on the basis of the
forcesof interatomic interaction. Special interest is further
caused by investigations of electric resistance @especially
-he ferro-_
at low temperatures), of the domain.structure-of t
magnetic crystals, as@well as of photoelectric and optical
Card 1/3 quantities. The present paper:presents a clear survey of what

SOV@53-67-4-3/7
Thread-shaped Crystals With a Strength That Is Near T eoretical Strength
,ives d t 1 s
has hitherto been achieved. Part I of-the-paper f, e ail
(with numerous figures) concerning the, formation,orientation,
and shape of-the whiskers; breeding by the regeneration of.
metals from their salts, and breeding by means of condensation
from vapors, and other methods are dacribed, as.also.the pro-
duction of nonmetallic whiskers; a number of, phot ographs
shows the shape and growth of copper- and tin-whiskers con-
siderably enlarged (Up to.9000 times). Part II.contains a
very vivid depcription of the growth of such..crystals as well
as data concerning a large number of papers, which are given
in a table covering two pages. Part III deals.with experiments
and results concerning the mechanical properties of the whiskers;
among other things, experimental data on the deformation of
whiskers are compared with those of ordinary crystals; the
tearing of these whiskers with as well as without previous
plastic deformation is investigated and described in diagrams
The creeping of metallic whiskers is described (also the:creep-
ing resistance of whiskers is considerably greater than that,
of ordinary crystals of the same material). Finally, the,
influence exercised by temperature and by the.dimensions of
Card 2/3 whiskers on "heir strength is described as also the influence

"@O 0 68691
P.2 00
S/180/60/000/01/015/027
E193/E135
AUTHOR: Rozenberg., V.M. (Moscow)
TITLE: the Relationship between Grain-Boundar3@Slipping and
Deformation within the Grains during_2r @e
PERIODICAL: Izvestiya Akademii nauk SSSR,Otdeleniye,tekhnicheskikh
nauk, Metallurgiya i I@toplivo,1960,Nr 1@ pp:105-110 (USSR)
ABSTRACT: It is a:well established fact that there is a close
relationship between the grain-boundary slipping and.
deformation of grains during creep .(Refs 1-3); the
relationship is.linear and,holds for all stages.of creep,
i.e. it is not dependent on the-rate of deformation
The linear character of this relationship indicates clearly
that,under certain given conditions, the process of creep
in all its stages is determined by one mode of deformation.
However, the question whether grain-boundary slipping.or
the deformation within the grains,is paramount, remains
still unanswered. MacLean and Farmer (Ref:l) who.had
inves.tigated,creep of an age-hardening copper-berrylium-,:,
alloy, and Martin et al (Ref 4) who had studied creep o
Card
brass, in erred fr
1/8 f om their, results that deformation
within the grains is the governing process. In the fl

68691
8/180/60/000/01/015/027
E193/E13 5
The Relationship between.Grain-Boundary..Slipping and Deformation:.
within the Grains during Creep
opinion of the present author these conclusions. are not.
justified and he considered.that more useful information
could be obtained by studying creep at a certain constant
temperature and.determining the part played by:both
grain-boundaryslipping and grain deformation,on a
specimen in which it would.be possible to vary the resis-
tance of the grains.to deformation withou@,changingtheir
size or chemical composition, It.was decided that the.
70Fe-3ONi alloy,would be most suitable,for this purpose.
This alloy,constitutes a y solid Solution with a phase-,
centered cubic crystal structure; on cooling below room
temperature the alloy,undergoes a y to a transformationo
similar to the austenite to martensite transformation.4
on subsequent heating above 5500C, an: a. toly trans.-
formation, also martensitic in character, takes place.
It has-been shown by several workers (Refs 5-7):that -the
Card Y -4 ct --:-kY transformation.brings about@fragmentation of
2/ 8 the soli@ solution-grains,into.a large number-of small
regions, which is accompanied. by distortion of the

68691
s/l8o/6o/ooo/ol/ol5/027
E193/19135
"The'Relationship between Grain-Boundary.Slipping and Peformation
within the Grains during Creep
crystal lattice at the boundaries of these regions: the
metal in this condition is thuscharacterized.by the
presence of alarge number of demarea'tion,planes (sub-,
boundaries) in.the grains which-have.retained their
original size, It has been shown, also. that the resis-
tance to creep,(at 770. 0C) of specimens that have under-
gone the @ y -@p m -
> y transformation.is lower than that
of untransformed alloy. Since raisin g:,the temperature of
the preliminary annealing from 8,00 to 1100 OC:reduces the
difference between the resistance to-creep of transformed
and untransformed specimensl and s,ince.this effectis
obviously associated with.the number of latticedefects
due to the y --@:a -@,y transformation:being,reduced by a
hi.gh-temperature,annealg itwas concluded that comparison
of the total elongation in creep,with the elongation due
to grain-boundary slipping,.measured on,t,ransformed and.,
Untransformed materialg would.make it possible to
Card
determine,the effect of the grain structure on the
3/8
behaviour of the grain boundaries in creep. :To make sure.

68691
S/180/60/000/01/015/027
9193/E135
The Relationship between Grain-Boundary Slipping and-Deformation.
within the Grains during Creep
that any of the observed,effects were.not caused by
changes in the grain boundaties@themselvesl it was
decided to carry out an additional series.of tests on
single crystal specimens. The composition of the
experimental alloy (prepared by vacuum melting technique)
was: 30% Ni. 0.4% Ti,*0.15% Mn remainder.Fe. Single
crystals were prepared by the pulling-up technique, the
polycrystalline specimens by the normal, mechanical
treatment methods., The single crystal.test pieces w .ere
cut from one single crystal by means.of.spark-machiningi
care being taken.to ensure@that the orientation of:both
test pieces in respect.:to the axis of:load was the same:
the dimension of the gauge length.of these test pieces was
2 x 1 x l0mm.: The dimensions,of the.gauge length of@the
polycrystalline test pieces were 3*x 2 x:25 mm. All the,
@test.pieces were~poli-qhedl.first.mechanicallyg,and then
electrolyti6ally@in a:
95% acett anhydride plus 5%
Card 'pieces were annealed
hydrochloric acid.mixture.i All.test
)+/8
at 1350 OP, for 2'hou'rs and cooled;in the furnace to r

68691
S/1806o/ooo/ol/o15/027
-E
193/E135
'The Relationship@between Grain-Boundary Slipping and Deformation
within the'Grains during'Creep
temperature (first type of heat treatment); part of the
annealed test pieces was cooled in liquid nitro en
Y -@-+ a t.ransformat-ion) and then.heated to 750 9C, held
at,,that,'temperature,for 6 hours ( a -) y transformation)
and cooled, in vacuumq t Ioroom temperature (second type
of heat treatment). The creep tests were conducted in.:
vacuum (lo-3 mm Hg) at 700 OC under,the stress of
2.5 kg/MM2; -periodically the tests:were interrupted to
measure:the total deformation and (in the case of the
polyarysta.lline sDecimens) the deformation due to the
grain-boundary.movement. The creep curves forthe single
crystal specimens,are reproduced in Fig 1, where curves
a.. and b relate to specimens subjected to the
preliminary heat treatment of the first and second types
respectively. It will be seen that the annealed crystal
deformed at a much slower.rate than the specimen which had
Card undergone the y -) a -) y transformation. This indicates
5/8 that shortening of the time-to-rupture and increased rate
of creep of austenite after martensitic transformation5

68691
S/180/60/000/01/015/027@@
E193/E135
The Relationship between Grain-Boundary.Slipping and Deformation
within the Grains during Creep.
The creep curves versus h) for,.
00
polycrystalline specimens, subjected to the preliminary
'heat treatment.of the first and second type, are
reproduced in Fig 2 (curves A and b,,respectively); the
-f (microns) versus V(h) curves for the same specimens
are reproduced in Fig 3. Here again, the rate of.creep of
the annealed specimens was slower than that of the
specimens @that had undergone the :'y_--@ a -) y trans-
formation.'@Since metallographic examination has failed to
reveal any int6rgranular cracksq it.'follows that the
deformation within the grain, 9cl@q is gi.ven by@
e the (microns).versus- relation-
eck':= eo@_ r i@ eck
ship.is illustrated by the graphs in Fig Thus, the
foll wingfacts have been established., (1) the resistance
0
to creep of a solid solution that has undergone the
-@.m --),y ttransformation is lower than that of the same
@solution in the annealed condition;@,(2) since this
card
7/8 decrease in the resistance to creep has been observed also
in single crystals,,it can be assumed that it is mainly
J

J" 6 /6,
- 0/00? /0@ '0 1
E-0 Si C- y-D T,1
AUTHORS: acs-enberg If i a;-
----------------------
TITLE: A St-ody of Grain-Bouardary Dis-plan-ement i n C' 1e e p
PERIODICAL: F-izika metallov k1netallovedExiye !960 Vol Nr 1
p1p, 12L--132 (USSR)
ABSTRACT; t, -n b -ou rvia r y
The authors repo2rt their -in-vestigatioz) Df gral
J-
displacement due to an]-argemen' of ,-ome g--@a-ns at th e
exDertse (.,,f' ol@hers d@-iring creep c!f' Figs 1 and
2 slhow tl-.@e also calliT b&-andary migration.
The object -wras the elucidation cif tbe 01- u t
e ect, in creeu and, the in,f'lulence of tixe boundary
lo(-at-ion wizli '--espeCt to 'thle extension. axis and o f, t-1 h e
mutual orientat-c the ex t ent
-i-n of neighbouring grains or-
(90.0(?
of dispiac,@!mant- A-lumninium witb traces of Ylgl
L
Si and Cu was used e -@.,orking pa-.-t of a specimet e i ng
I Lh n b
x Y, 50 mm Annealinc- for 1 hour at LOO G%" gave a
mean. grain diameter of 0.2 mm, unaffe,-ted by p@--olonged
heating at 275-3-25 cc. Specimens @14-ith ground and,
0 1 e t-r-0 I Y t call surfaces were tested at_La
pollstied
Card of @O,Ir jCg/mg,2
COnstant load criving an initial st-ress
3@oecimens were removed from the machine at a carLai."'L.

S/'11,2-_b/_-0/009/01/023/031
Bill/B191
A Study of Grain-Boundary D-J'splacament in Creep
stage of Creer, and tho extent of mi.igration of 100
L
-oundar es -vas n.-Leasured microscopically (differentiation
fropi movement of one gra-in relative to anoth.er being
e f fe c, t ed as shown schematically in Fig 3) C; r e e. p ourves
th
300 and 325 OC. are shown in @ Fi
obtained a t 2
corresponding @!alues of average displacement being gi,*,en
_JZ! Fig 5, Fig 6 shows these values Dlotited asainSt
deformatior, while Fig 7 givas relations between tha
lo_@;-arit'hms of the ti'me to obtain di-S-placement's of 2@
and l.q and! the reel-procal of absolute temperat7ire.
These re-iations.are linear-, ind,icating an a,-tivation_
energy of -1 K
188 kcal/moi, Use olf this value in the
applropi-iate equation enables the curves of Fig rej-ating
to three dif,"If'erent teirpe--ratures to represented by a
sin,-:Ile clarve (Fig 8)@ kgreement- with- the dat-d of _Harpw@,
Siiepard ancl Dorn (Ref D') is shown by Vine- reSults JL7r - FJ-g '91
Card t,1.7,c- -,.-alue of the. displal-emen-t.. a'Lcr-,-,a bo-un-da-'Y'
2/-) cvement s rela t v e to . ea -h @her) is :01
.-e- g7ain a L ve'
a -@airis t ti angle bez a t@_,e spef:timer, axis and the
ra r@@a_
1 the.- boundary on the- CG and @a

6 i,54 b 3
S/126/6o/009/01/0'-3/103i
E.11.1/El91
A Study cX Gra-in-,Roundary D.-ILsplacemarit- in Creep
deformatica, o--:' a maxlurcam,ccc-drs cttl:'!-,,':,, OC, an(@ the
1--west, -,7alues a, t 0 ah,," 900 Fig: '-0. shows til@
abs@@nce of cori @---,atio-n be,",ween- this aii4s; and the
cou,ndary T'01c- authors note tliat 1:
t t j. 11
ur.certai-ri whothe-1, the toundarv, @Ls d.!sL'-,I.c3.c-.ed -f'roma gra In
-le r to One nf p
h; -1 -Gwer eiasti -ne--r,-y ur 'Tricc versa
, -er t@ nt The
n .T ;ornmand invest ation r,
a poi
dis-ol-a-cement eertairlY leads to a r e du. c t I o P- ir tntal
6h L,
elastic energy of neighbouring ggrain-@ and 6@ @ 9 ma - er ia-,
as a whr;le. and 1)1-asti@-!Lt
y InCreases,
The@.e al-a. 10 figures@ 2 tables and'. 9 referances, o --F whish
Card
are 3 Bngl-i-sh4 2, Fre-m'-th and, _7 frorin Act"a
3/3 Retal-lurgica.
ASSOCIATION: Inst4tut- me tallof izikl; - TsNII(.Td,1 (Metall-physics
(I,-SU1kute of Tsi-111cu")
SUBMITTED: September 1959

8.0890
9073/E335
AUTHOR R enberg, V.M.
"z
n
ITL T
T E Slow Defo,,.tion %f Single CrXstals of/iron nickel
Solid Solution at. Elevated Temperatures
PERIODICAL- Fizika metall ov i metallovedeniye, 196o, V61 -9,- Nr 6,
pp 922 926 (ussn)
ABSTRACT: It was established earlier that depending on the test
conditions phase work-hardening maIyIlead,to an increase
or to a decrease in@.the strength. Specxmens,subjected
to phase work-hardening as a, result.of loading,over-long
0
periods at elevated temperatures (700 C) have a lower.
strength than specimens which were not subjected to phase
work-hardening. :This difference is due to structural
trans'formations,leading to a change in the grain properties,
but it canalso-be due.to a change in the mechanism of
deformation, whieh dependson the initial structure of the
material. To verify the latter, it is adv1sable to
investigate micro.sc.opi-cally the picture occuring in the
case of.creep of solid-solution.specimens. To eliminate
the influence of grain boundaries such investigations are
Cardl/4 best carried:out on single crystals. In the experiments

80890
S/126/6o/o69/06/018/025'
EOJVE3-@
'Slow Deformation of Single- Crystals o, an I on-nickel Solid Solution
at Elevated Temperatures
described in this paper, an alloy containing 300% Ni
Ti, 0-15%,Mn, rest Fe was used. An Alloy ofthis.
composition represents asolid solution with a face-,.
centred cubic lattice. On c,ooling the y-solid solution
below room temperature a martensitle y4a transformation
takes place. Heating of the transformed a-solld solution
0
above 500 C leads to a reverse, a-A-y transformation,
which is also of the-martensitic type. The y-@a-37y trans-
formation brings about afragmentation ofthe y-phase
cilystals into numerous small areas,',disrupting the regular
structure,at the.boundarles of these areas. Such chan Iges
in the intracrystalline'structure lead to property changes.
Two specimens, 2'x 1 x 10 mm', were.produc.ed by electro-
eros IIon cutting of a single.-cr'ystal; orlqntation,lof both
relative to.the tenstle-stress axis was equal. According
17t
to analysis, sliding hese crystals should proceed in the
plane , (111) in' the direction rl!01.. Both-specimens
0
were annealed at 1 ?50 @C.for two hours and cooled to
room temperature in the furnace. Then one of the specim ns
Card2/4

80890
s/i26/6o/oo9/o6/oi8/025
EOJ@OF-3R2
Slow Deformation of Single Crystals of an H7 ckel Solid Solution
at Elevated Temperatures.,
was cooled in liquid nitrogenand subsequently heated
0
(in vacuum) to 750 C and held at that temperaturefor.
six hours, thus transforming it into@the y-phase - The
0
specimens were tested at 700 @C with a tensile load,of
2
2.5 kg/mm Xn vacuum. Aftersome stretching, the specimen
was relieved of the load, cooled and removedfrom the
vacuum chamber..,The total elongation was measured and
the surface was subjected.to metallographIc investigation.
After fracture, the reliefoccurrIng.,at the surface of
the specimens was studi ed, by means , of_ aq int@.erf erenc e
microscope and,the.change in the orientation of.the crystals
relative to the tensile-stress,axis was determined by
X-ray diffraction. The obtained data lead to the
conclusion that the difference in the behaviour of an
annealed.specimen and a specimen which-was subjected to
phas.e work-hardening is riot due to qualitative changes
in the dbformation mechanism. Due to the presence of-
Card3/4 lattice defectsin.the transformed-specimen the process
of sliding will be more intensive in it thanin, anneale4_,.,"
specimens.

82641
S/126/60/010/02/011/02.0
E021/E335
AUTHORS: Gorelik,_S.S., Kallyanova, S.M. and,Rozenberg, V.M.
@TITLE: Structural Changes in Aluminium With Slight Deformation
and a Subsequent Annealing A
PERIODICAL: Fizika metallov i metallovedeniye, 19609 Vol. 10,
No. 2, pp. 251 - 261
TEXT: AV-000 aluminium containing traces.of magnesium, silicon
and copper was used in the investigation. Deformation was
produced on a 5-ton press at 21 mm/min. The number of slip
.marks, the vertical component of displacement in the slip marks
and the vertical component of displacement of grains relati--xe
to:one another were measured.on an interference microscope by the
method described in earlier work (Ref. 3). The mean grain size
was also found. M�gration of the grain boundaries during re-
'crystallisation was found by a method.using pol@arised light
(Ref. 5). The critical degre e of deformation using 1. an annealing
temperature of 400 OC --ras.found:by..construct�ng a graph of grain
size after annealing against de'gree,of deformation.-It was found,
to be approximately 6-50"0. Fig. 2. shows the influence of small
degrees.of deformation on the number of slip marks, the mean dis-
Card 1/3

8261a
s/126/60/010/02/011/020
E021/E335 :
Structural Changes in Aluminium With Slight Deformation and a,,
Subsequent Annealing
placement in the slip marks, the mean displacement between the
'grains and the ratio of the.last two, in descending order. This
shows that the basic.mech,anilsm.of,plastic flow, with or:without
the criticaldegree of deformation, is the-same - slip in the
grains accompanied by,displacement.of,the grains, relative to one:
another. After deformati-on'less'than the critical value,
siructural-changes during annealing occur, in the main, by
polygonisation, with a small degree of,migration of boundaries
of individual grains, stimulated@by the tendency to decr,ease the
surface energy of a system (Figs- 3, 4).. Very occasionally,
migration of the boundarj: occurs because of differences.in volume'
energy of adjacent grains (Fig. 5). After-deformation greater
than the critical amount, annealing-at 40b 'C is accompanied@by,.,
intensive growth of individual,crystallites and frontal,migration
of boundaries which is stimulated by differences in.volume
el astic energy of adjacent grains. The, rate and distance of
migration of bounda ted
ries is many times greater than.that stimulat
by surface energy differencesu Intensive growth occurs afteran
Card 2/3

82641
S/12,6/60/010/02/011/020
E021/E335
Structural Changes in Alumi,nium With Slight Deformation and a
Subsequent Annealing
@incubation period during -which,redistribution of theenergy
inside the grains occurs (Figs. 6-8). After deformation many
times greater than the critical amount, new grains arise between
the original grains at places of maximum distortion. The
orientation of the new grains differs sharply from those
surrounding it. This occurs after an incubation period of 6
to 30 minutes. There are 8 figures, I table and 7 references,
6 Soviet and 1 English.
ASSOCIATION.o TsNIIChM
SUBMITTED: March 19, 1960
Card 3/3

---------------- r-
ACC NRt AimV SOURCE CODE B070 E070
58/65/000 0
AUTHOR: Rozenberg, V. M.
TITLE: Fine slipping during creep
SOURCE: Ref. zh. Fizika, Ab s. 12E537
REF SOURCE: Sb. tr. In-t metalloved. i fiz. metallov Tsentr. n.-i. ift-ta chernoy me-
tallurgii, vYP- 36, 1964) 67-76
TOPIC TAGS: creep mechanism, crystal deformation, nickely physical diffusion
ABSTRACT: The nature of the total-odeformation fraction (ix).whose tracks cannot.be.
observed on the sample surfac%ly ordinary optical microscopy,was investigated in
singleAnd polyerys'tals of Ni. Itis,established.that'rm varies with the temperature
and stress in the same manner, as the part of the defo;m;fion due to the coarse slip'
tracks. @x is 4 - 8 orders of magnitude larger than the rate of deformation estimated
on the basis of the theory:of diffusion creep. These, and also some other data given,
in the article, give grounds fora Iasuming that the.deforma It.ion whose tracks cannot be
observed by metallographic ethodsp'is:the result of fine slip. V. Rozenberg. (Trans
lation of abstract
SM CODE: 20
Card Vj-

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v to
.

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SUBMITTEDC--@--*@ 0,0-@:@I@lf'-.t@:@'--
me all. tb
a 0- me

W776/62/000/024/002/007
EIII/E135
AUTIIURS Vinograd, M.I.? Rozenberg, VANI., and Shapiro,
TITLE: Modern methods
for phase analysis of steel and alloys
SOURCE: Noscoly". TsentralInyy nauchno-is'sledovatel'skiy xnstitut
chernoy metallurgii. Sbornik trudov ' no. 24, 190U.
Novyye metody ispytaniy wetallov. 191-203.
TEXT: Phase analysis is important. in developing new materials
,with special properties and in improving existing inaterials. The,
authors outline the characteristics of four main groups of methods
available: wetallographic, X-ray, chemical and electrochemical,
physical. As examples of their application to the solution of,
currently important problems the authors discuss tile following: i
low strength of weld in tubes of type 1Y,1849S (lKhl6N98) steel;
formation of sigma-phase in high-silicon steels and alloys, leading'.
to loss of ductility; low plasticity in tensile tests on some
heats of type X2-5 (Kh25) steel; excessIve inc-fusion content in
type 0 )(18 Hi 9 T , (OhhlbNW), steel; estimation of.inclusion content
in high-purity steels, e.g. type LUX15 (ShKhl5); failure of steel
in hot mechanical deformation.
Card 1/2

9754
Z
S
26/62/ol4/oOl/010/018
E193/F,383
AUTHOR: Ro z enb erg.... V. N.
TITLE: A study'of creep of nickel single crystals
PERIODICAL: Fizlka metallov i metallovedeniye, v. 14, no..l,
1962, 114 120
T &,T: The main shortcoming of creep tests carried-out on
polycrystalline specxmens as thatthe results'may be affected to
various degrees by the presence of grain boundaries, and,
consequently, may not be easy to interpret in terms of basic
la-v-ts governin-,r theiphenomenon of creep. This prompted.the
aut'nors to undertake the investigation described in the present
paper.- To ensure the same orientation and degx7ee of purity in
all 'the test pieces, they were cut from one" N! single crystal,
p,repared by the conventional pulling-out technique. The creep
tests were carried out in vacuum at 670 7700C under'a stress.
2
varying from 350 - 1 190 z/mm It was found that under the
rate
conditions employed the of steady creep is
described by:
Card l/

S/126/62/014/ool/olo/ol8
A study of creep of E193/E383
n
E A exp (-67 OOO/RT) where, is the applied stress
T temperature and n 4.4. This relationship was found to
be in mood agreement with that based on Weertman's theory of
clitab of dislocations, which means that diffusion-controlled
rela_-,@at�on is the slowest of the processes determining the rate
of steady creep. Using the Weertman equation and ex@eriment-al`
data obtained in the course of the present investigation, the
author derived formulae for the density of sources on-dis-
locations 'M at. a constant temperatuzra:
9
M 2 x 10-76 2 cm-3 (5)
and at a constant stress;
exp(-38 000@T)@2
M 3 x 11035 (6)
Tz
@j C.
.Card 2/ 4

S/126/62/014/001/010/018
A study of creep .... E193/E383
9 10 10 cm-3 for the t re-
The values of M were 10 emperatu
and stress ran-es studied. These values were in good agrreerjent
with those calculated from data on the size of subgrains and:
the degree of their misalignment, which confirmed the validity
of the equation derived by the present author. Data on creep
of. single crystals were correlated, in the final stage of., the
Investi-ation,-with those obtained by Weertman and Shahinian
(Tans. AIME, 19516, 206, 1223) on polycrys'talline specimens. The
resul' ts - aE e reproduced in Fig. 6, where (Z Tep Q/kT)/LLI..
OC/min. cin is plotted against stress (dyne/cm here, -L and
LI denote, respectively, the size of grains and subgrains.,
the tvlanZles and squares relating to creep@of polycrystalline
specim6ns at temperatures indicated in the.insert,othe circles
670 - 730 C- 'It Will A
rel'ating to creep of-single crystals at
be seen that this relationship is similar for both'single-
crystal and polycrystalline material, which indicates that the
@presence of grain boundarles does not. give rise to the appearance
9f a sQparate.mechanism,..of deformation, making asubstantial
contribution to the total deformation in creep.
There are 6 figures.,
CArd 3/4

5/126/62/o14/001/010/018
A study of creep E193/E383
ASSOCIATION: Institut metallovedeniya i fiziki m.et:allo.v
TsNIIClu%l . (Institute of Metal Science and Phys 3'. C S
of Metals, TsNIIChM)
FTJBIIITTED.- October 31, 19G1 (initially)
41
January 2 1962 (after revisio
Fig. 6: 66000 raly-rica,
-.4 &,goo*. n0,1UKPUCma1?,?b1
fo 81/000
j 0 crysft.13
W C OUCMt7"
v10M 7
A
/0
00
101
Card 4/4

S/126/62/013/006/009/018:'
E021/E192
AUTHOR: ..Rozenberg V.M.
TITLE: ..The nature of the part of deformation not detected in
microstructure during the creep of nickel
PERIODICAL: Fizika metallov i metallovedeniyo,'v.13, no.6, 1962,
894-900
TEXT: Experiments were carried out on nickel single crystals
in order to show how much deformation was caused by visible slip.
lines and how much deformation was not connected with observab]
structural changes. Specimens (2 x 3 X 10 mm) were cut from a
single crystal of nickel (99.95%) with the strain axis and the
observed*surface disaligned by not more than 2-30'. -They were
heated in vacuo at 1150 *C for 6 hours and electrolytically
polished prior to test. Testing was carried out in vacuo at
@670-770 *C with shearing stresses of:450 to 1190 8/mm 2.
Occasionally the specimens.were unloaded, cooled, and after
removing from the apparatus, the.elongation, number [e-mail]
on the &@Luge length.and height of slip lines were measured. The
total elongation,was measured on a microscope andthe remaining
Card 1/2

S/126/62/013/oo6/ooq/ol8
The nature of the part of deformation... E021/E192
measurements were carried out by an interference microscope. it
was established that not-all the deformation is localised in the
slip lines visible under the microscope. The deformation not
visible, under the microscope (ex) is obtained bysubtracting the
deformation due to observed slip lines (ese) from the total
dePor-mation. In the investigated ranges of stress and 'temperature
Ex is greater than Est. Both Ex and Est when plotted against time
show a period of decreasing rate of creep and then a region of
steady-state creep. For ex, es? and etotal, the rate of change of
deformation with time is proportional to time to the power of 4 '4.
The possible rate of creep due to diffusion mechanism cain be found,
knowing the coefficient of diffusion fornickel. It is lower than'
the exi3erimental values observed for ex by a factor of.,,8-9. Thus,,
Ex is caused by crystallographic slip and...not by adiffusion,
mechanism. There are*10 figures and 2 tabless
''ASSOCIATIONI Institut metallovedeniya @ fiziki metallov TsNIIChM
(Institute of Science of tletals and Physies.oflltetaisl.
TsN11ChM1)
SUBMITTED: Septembez-.20, 1961
Card 2/2

S/126/62/,013/003/023/023
E021/El8o
AUTHORS: Voloshina, L.A., and Rozenberg, V. M.
TITLE: Influence-of the orientation of aluminium single J
crystals on creep
PERIODICAL: Fizika metallov i metallovedeniye, v-13, no-3, 1962,.
11711-476
TEXT: Single crystals of 99. 991/0' a luminium were, prepared by
selective recrystallization. The gauge length of the specimen
was 25 ameter 6 m:.q. -lith stress of 1164 g/mm2
nim and its di, a at
20@OC, a sample in which a large number of slip systems could,
operate deformed much less than a sample in which the.probability
of slip was, extremely small except in the main system. After ten
,hours the crystals deformed to 3.2 and 22..5@o* respectively.
At 300 OC,,with a stress of 124 g/mm2, the behaviour was reversed...
The results conf4.rmed that a large number of slip systems results
in strengthening at low temperatures and an increase in
deformation at higher temperatures. It had been shown (Ref.'6:,.
D. MacLean, Grain Boundaries in Metals (Granitsy zeren v
metallakh), DIetallurgizdat, 1960) that slip in grain boundary
Card 1/2

influence of the orientation of ... S/126/62/013/003/023/02 @3
E02l/El8O
regions of polycrystalline samples.,was complex. In these regions,.'
in the case of a face-centred cubic lattice, up to.five families
of slip can operate. Thus, at low temperatures, this would
result in strengthening, and at higher temperatures in an increase
in deformation. In this way, the effect of grain:size, on creep
resistance could be explained without the idea of the "viscous
behaviour$, of the boundary.
There are 3 figures.
Z'
ASSOCIATION; Inst:Ltut metallofiziki TsNIICh1-1
(Institute of Physics of Metals, TsNIICh1-1)
SUBMITTED; July 17, ig6l
Cavd 2/2

S/032/62/028/002/024/037
B124/B101
AUEHOR: Rozenberg, V. M.
TITLE; Evaluation of the values of elongation due to slide tracks
PERIODICAL: Zavodskaya laboratoriya, v. 28, no. 2, 1962, 219-222
TEXT: Values of elongation due to the displacement of a material in one.
track and the number of tracks per unit length of sample yield sufficient
data for the calculation of elongation due to all tracks in p9lycrystal.-
line materials and single crystals. The meandisplacement of.polycrystal-
line materials in one track can be determined by measuring the.height of
the tracks with the -.@interference microscope MHO-4 (MII-4). The, mean
elongation p due to one track is p = 2.3 h V1 + where .6-
total' . total
is the elongation of the whole sample. Hence,the deformation due to all
slide tracks is given by E 100%, where n is the number of slide
st
tracks per unit length of the initial sample. The schematic diagram shown
Card 1

S/032/62/028/002/024/037
Evaluation of the values of elongation ... B124/B101
in Fig. 2 is used to evaluate with X,Y, and Z being a system of
s
orthogonal coordinates related to the sample. Theelongation is given by
rhl+72
2
41 = - Ta -nA (5)9 and, for small values ofA, h 2 = Altanp. Hence,
Al = hj/@(tan 2A - tan 2p M- With the optical microscope, however, the
total height of the slide.track H=nh is measured, thecorresponding elongaa-
@H@j@ + H2
2 2 2
tion beingAL=nAl, for whichtL and AL = Hl/(/tan A - tan P)j_ re-
tan
spectively. A is measured by an X-ray method. The angle P andits,change
with,deformation were determined using stereographic:projection (Fig. 3).
The values of AL due to one slide track were calculated from Eqs. (5).and
(7) for slide on two faces of a nickel single crystal perpendicularto
each other. The accuracy of H measurement is examined on a single crystal
of nickel after 9.1%.deformation. H1 was found to be 0-113v which agrees
fairly well with.results calculated from Eqs. (5) and (7). The method
.,Card 2/4

S/032 '62/C,28/002/024/037,
1.1yaluation of the values of elGiigation ... 124/ loll
i B.
de3cribed can be used for coarse-grained materials, with thc, orientation
of the individual grains being determined from X-ray data and etch patterns,
rc'spectively. There are 5 figures, .1 table, and 5 references: I Sov Lit,
t -language publicaLtion -reads
and I non-Soviet. The.reference o -the English
as follows: ft. A'Aaddin, E. flarrisong R. Gelinas, Act-a ;,i,et. , no. it,
AS'o'OCI-ITION: Tsentrallnyy nauchno-issledovatel'skiy in,9titut chernoy
metallurgii im. I. P. Bardina (central scientific Rezearch
Inotit,,--Ae of Ferrous 'Metallurgy ihieni I. P.
Sche@:iatlc diau@raln of step formation due to dizlacc-e'n't alon.- tile
eli-u plane (p i.-i the displacement *vector; hV 'h2' --.-,.nd 1 are
comr-onents of the displacement vector)-
stereographic projection illustrating the methad. uscd to deter-
3.
(V noi@m-zl
mi--! the -angle :P. Legend: (A) plane of observation,,,. A
to [he G~~.mple.ourface;.(C),-directidn of slip; (D) axi6.01 el oy')c7aw-'
tioll-M slip plane.
Gayd 3 /4'_'

S-lLIRI,4'OV-AIYAYEV, Georgiy Aleksandrovich, prof., doktor tekhn. nauk5 GASTE%T,

2- 1
>92 S/126/61/012/001/014/020
E193/E48o
AUTHORS: Voloshina, L.A. and Rozenberg, V.M.
- ----------
TITLE., Investigation into the.creep of aluminium bi-crystals
PERIODICAL: Fizika metallov i metallovedardye, 1961, Vol.12, No.1,
pp.118-124
TEXT: The generally accepted view that the relative movement of
crystals plays an important part in deformation during creep is
based partly on the fact that grains stand up in relief on a
preliminarily polished surface of a specimen tested'in creep.
However, it can be postulated that this effect is caused'not by
crystal boundary sliding but by the fact that the adjacent crystals
are deformed in a different manner. The most convenient way of.
checking this theory is to conduct creep tests-on specimens on which
the. behaviour of any given grain boundary can be easily studied',
bi-crystal specimens being most suitable for this purpos. e.. The
effect of temperature, applied stress and degree of misorientation
between grains on the rate of creep and degree of deformation of
bi-crystals has been studied'by several workers. The object of the
present investigation was to measure the elongation of various parts
Card 1/7

25922 S/126/61/012/001/014/020
Investigation into the-creep ... E193/E48o
of an aluminium bi-crystal test piece with.a@particular reference.
to the grain-boundary regions and to study the micros Itructure of
,these regions. The bi-crystal specimens were. prepared from..
'AVOOO) grade aluminium by the usual method of annealing the
ASOOO
olightly deformed metal. The creep test pieces (with the parallel
''portion measuring 25 x 5 x 3 mm) were cut from the blanks in such a
way that the bi-crystal boundary was inclined at 45* to the test
'piece axis. The test pieces were annealed7at 6oo*C and
electrolytically polished, after which a set of thin scratches was,
,inscribed with an aluminium alloy scriber on the polished surface
All creep tests were carried out at 300% under an initial stress
of 0.2 kg/mm2. Each test was periodically interrupted and,
after co.oling.the test piece.toroom temperature, the total
elongation of the gauge length, the elongation ofeach crystal and.
the displacement of the scratches intersecting the grain-boundary
were measured, Metallographic and X-ray diffraction analyses of
the specimens were also carried out. Typical results are
.reproduced in,Fig.1, where the relative elongation (%)'is plotted
e (hours); this graph.was constructed for a test
gainst tim . -piece
'whose stereographic projection is illustrated'in Fig.2, where
Card 2/7

S/126/61/012/001/014/020
25922
Investigation into the creep E193/E480
continuous and broken lines relate to the first and second
crystals respectively; the plane of projection corresponds to the
specimen surface, the point in the centre of the projection
representing normal to the specimen surface; the arrow indicates
the direction of applied stress, The gauge length of the specimen
was divided into,5 Parts in the way shown in the insert in Fig.l.
Curve 1 in Fig.1 relates to the entire gauge length (i.e. to the
part of the test piece bounded by points 1 to 6) while curves 2, 3,,
4, 5 and,6 relate to parts bounded by points 1-2. 2-3, 3-4, 4-5 and
5-6 respectively. It will be seen that the rate of creep varied'
considerably from one part of the test piece to another. , It is
particularly significant that the rate,of creep of the part
containing the grain-boundary,@i.e. the part bounded by points 3-
.4 (curve 4), was slower than that of the adjacent parts, bounded by
points 2-3 and 4-5 (curves 3 and 5 respectively). Owing to the
difference in the orientation, the rate of creep of any part
belonging to the crystal bounded by points 1-3 was slower than the
,rate of creep of any part of the crystal bounded'.by points 4-6.
The results of other measurements are best summarized by:referring
to Fig,3. which shows diagrammatically the bi-crystal (a) before.
Card 3.' 7

25922 S/126/61/012/Ool/ol4/,020
Investigation into the crrdep ... E193/E480
and (b) after deformation; the symbol I in Fig 38 denotes the
grain-boundary displacement and x = 1 cos a is the component of
resolved in the direction of applied stress. it will be seen
from Fig.4, where x(ji) is plotted against the strain AE3-4G)
of - the part of. the test piece bounded' by points 3-4, that x- is
bylone order of magnitude smaller than &E3-4 and that.there is a,
definite (linear) relationship between these two parameters. By,
the process of elimination of the possible explanations of these
facts, the present authors showed that the observed displacement of
the grains is a result of the deformation of the grains in the, grain-
boundary region and not -ice versa, This conclusion was supported
by the results of the next series of measurements, whose results,
are reproduced in Fig.6, where the vertical component of
that is the height p of the step formed by the grain-boundary
displacement, is plotted against time (hours-), blocks 1- 7 showing
the magnitude of this component at various points along the grain-
boundary, as markedon the insert in Fig.6. It will be seen that
not only the height of the step varies along the grain-boundary
but that there is a point.at.which the grain-boundary displacement
throughout the duration of the creep test remains smaller than,at
Card 4/7

25922 S/126/61/012/0,01/01.4rOO2O
Investigation Into the creep ... E193/E480
any other.point; in addition@, the height.of the step at certain A
p6ints*of the grain-bound'ary..decreases.with,.time lsee@point,3,after-
14hours, Point 5 afte'r 40 hours,,etc). These,results,
correlated with the results of metallographic and.X-iray analysis,
show conclusively that the formation of stepi;*at'the grain-boundary
du.r.lng creep isnot caused by grain-boundary sliding (relative
-0
ii vement of the adjacent grains) but is,mainly a result of.the-
difference in the degree of deformation of the crystals.in,the
rer,ions adjacent to the grain-boundary. Acknowledgments are made
@to the student I.B.Finkellshteyn who participated in this work.,
There are 8 figures,..-l table and 8 references; 3 Sovket and'
5 non-Soviet. The four most.recent references to English langubLge-'@*
publications read as follows:, , McLean D., Farmer M.H. J.Inst.
Metals, 1956, October; Tung S.K., Maddin R., J.Metals, 1957;,9,:.'
NO-7, Sec., 2, 905; Rhine+s F.N., Borud W.E., Kissel M.A.' 2__
Trans'. ASM, 1956, 48, gig; Intrater J., Machlin E.S. J.Inst-.
M@tals, 1960, 88, No.7, 305.
ASSOCIATION: Institut metallovederxiya i fiziki metallov TsNIIChM
(Institute of I-fetal Science and Phys.ics of Metals
SUBMITTED; Septer.-iber 9, @1960 TsNIIChM)
Card 5/7
Wo. _001-A i N _09-4
0_6

80890
S/l26/6o/ooq/o6/ol8/O25:
"E073/E335
AUTHOR: fRozenber"'_@ V.M.
an
Single Crystals of/lron-ni. el
TITLE.: c@-S@j'o iv , D f ck
Solid Solution at Elevated.Temperatures
PERIODICAL. Fizika metallov i metallovedeniye7 1960, Vol -9-. Nr 6
pp 922 - 926 (ussn)
ABSTRACT-. It was established earlier that depending on the test
conditions phase work-hardening may lead toan Increase
or to a decrease in the strength. Specimens subjected
to phase work-hardeninglas Ia result of loading over long
periods at elevated temperatures: (700 0C): have.a lower
strength than specimexis which were not subjected to phase
work-hardening. This difference is due to structural
transformations leading to a change in thegrain properties
but it can also,bedueto a, change in the mechanism of.
deformation, whlch-.depends.on the initial structure of the
material. To verify the latter, it is,advisable to
investigate microscopically thel,picture..occ,uring in the
case.of,creep.of solld-solution specimens.@ To eliminate
the influence of:grain,,boundaries such investigations are
Cardi/4 best carried.out ion single cry.stals. In the experiments

80890
.8/126/60/dog/o6/ol8/025
E013/E
a 31&n-nickel Solid Solution
Slow Deformation of Single Crystals o, n.
at Elevated Temperatures
described in this paper, an alloy containing,300/ Ni
o.4-,,' Ti, 0.1550' Mn, rest Fe was, used. An @alloy of this
composition represents a solid solution with a face-
centred cubic lattice. On cooling the y-solid solution
below room temperature a martensitic y,4a transformation
takes place. Heating of the transformed a-soli,d solution.
above 500 OC leads to a reverse, a-@,^( transformation,
which is also of the martensitic type. The y-@a-7y trans-
formation brings about a fragmentation of -the y-phase
crystals into numerous,small areas., disrupting the regular
structure at the boundaries of these areas. Such changes
in the intracrystalline structure lead to property changes.-
Two specimens, 2 x I x 10 mm, were produced by electro-
erosion cutting of a single-crystal; orientation of both
relative to the tensi-le-stress axis was equal. According
17these crystals should roce d 'n.,the
to, analysis, sliding
plane (111) in the @ direction . fi!01 Both specimens
were annealed at. 1 350:'C for,two hours'and cooled to
room temperature in the furnac e. Then one of the specimens
Card2/4

80890
S/l26/6o/oo9/o6/ol8/025
EOJ@/U@@ckel.So
Slow Deformation of Single Crystals of an n-. lid Solution-
at Elevated Temperatures
was cooled in liquid nitrogen and subsequently heated
0
(in vacuum) to 750 C and held at that temperature for
six hours, thus transforming it into the y-phase. The
0 0
specimens were tested at 700 C with a tensile load of
2
2.5 kg/mm in vacuum. After some stretching, the specimen
was relieved of the load, cooled and removedfrom the
vacuum chamber. The total elongation was measured.and
the surface was subjected to metallograpliic,.investigation..
After fracture, the relief occurring at the surface of
the specimens was studied by means of aqint-erference
microscope and the change in the orientation of the crystals
relative to the tensile-stress axis was determined by
X-ray diffraction. The obtained data lead.to the
conclusion that the difference, in the behaviour of an.
annealed specimen and a specimen which was.subiected to
phase work-hardening is not due to qualitative changes
in the dj@formation mechanism. Due to the presence,of,
Card3/4 lattice defects in the transformed specimen the process
of sliding will be more intensi-ve in it than in anneal
specimens.

26561 S/126/61/012/002/011/019
ti EI021/E480
,AUTHORS: Voloshina,-L.X., jozenberg, V._M_ and Finkel'shtevn, I.B..1.
TITLE. The connection between boundary migration and'
deformation in the boundary zones during the creep o If
metals
PERIODICAL: Fizika metallov i metallovedeniye, 1961, V.ol.12, No.2,''
pp.265 _268
TEXT:_ Experiments were carried out on bicrystals of aluminium.
The boundary between the crystals was at 450 to the strain axis
of the sample. A stress of 200 g/mm2 and a temperature of 3000C
were used. Lines intersecting the grain boundary were drawn on.
the electropolished surface before test. During the creep test,
the relative displacement of the lines (in the plane of
-observation) was measured by an-interference microscope. Fig.2
shows (in microns) the relative displacement of the grains (circles),
and the migration of the boundary (triangles) against time (in hours).
Fig.3 shows a microphotograph of the bicrystal taken on the
interference microscope (x280) and Fig.4 the profile of the same-
,sample at the grain boundary. The data show that deformation in
Card 1/4

s/i26/61/012/002/011/019
tlo5u
The connection,between 61dary ... E021/E48o
n
the boundary regions is not stopped when migration of the
boundary occurs., Thus, the alternate.relative,displacement of
grains and migration of boundary, as proposed in Ref.l@(Chang H.C.
Grant N.J. J.Metals, 1952, No.6, 619) to explain the cyclic
character of the deformation-process in the boundary regions,
is impossible. It is proposed that the cyclic nature of the
process is caused by alternate hardening and softening, the
softening in this case being connected with boundary migration.
There are 4 figures and 11 references: 5 Soviet,and 6.non-Soviet...
The four most recent references to English language publications
read as follows:
Chang H.C., Grant N.J. J.Metals, 1952, No.6, 61g;
Rhines F.N., Bound W.E., Kissel M.A., Trans..ASM 1956 48, 919;
Tung S.K.,,Maddin R. J.Metals, 1957, 9, N7, sec.2, 905;
McLean D., Rev. met., 1956, 53, 139.
-ASSOCIATION: Institut metallovedeniya i fiziki metallov,TsNIIChM
(institute of Science of Metals and-Pbysics of
Metals TsNIIChM)
.SUBMITTED: 'December 19, 1966
Card 2/4

24478
S/126/61/011/006/004/011
E193/E483
AUTHOR: Rozenberg. V.M.,
,TITLE: The effect of substructure on creep if nickel
PERIODICAL: Fizika metallov i metallovedeniye, 1961, Vol.11, No.6,
pp.899-909
TEXT: The effect of preliminary heat and mechanicaltreatment on
the rate.of creep hasbeen quite extensively studied, Thus, for
:1.11stance, D.McLean and A.S.L.Tate (Ref,l: Rev,met,, 1951, 48
No-10. 765) showed that polygonization of aluminium grains,
attained by rolling and subsequent annealing, reduced,the@rate of,
creIep of this nfetal at 2000C,by a factor of@200 to 500,0- Similar
results were obtai-ned by other workers who, however,,did not
investigate the elementary processes associated with th,e
de f o riaa t ion in creep. The object of the present inve'stigation was
to study tile effect of.substructure on both intra- and inter-
crystalline deformationin creep of nickel, which had been selected
for this.purpose because of the existenceof a large body of
nsity of
experimentil evidence.on creep of this.metal and on the de
.sub-boundaries after plastic deformation followed by annealing.
Card 1/9

S/126/61/011/006/004/011
The effect of substructure E193/E483
Nickel of 99.9% purity with traces of Al, Si, C Iu, Co and-Fe was
used in the experiments. It was established in a series of
.preliminary tests that if this malterial is plastically deformed,
(at room temperature) to less than 6% deformation, no new.grains
are formed on subsequent heating to 8000C. The flat creep ' test
pieces used by the present author (with the gauge length measuring
40 X 3'x 2 mm) were polished and vacuum annealed at 11500C for
2-3 hours. after which the average grain-size was 0.165 mm. They
were then plastically deformed (at room temperature) in tension at
a rate of strain of approx 30 mm/min to attain elongation varying
between 0 and 6%, annealed at 800% for 1 hour, and
electrolytically polished. (In every case the average grain-size
of the specimen remained equal to 0.165 mm.) The creep tests
were all carried out in vacuum at 7000C and under a stress of
2.5 kglmm2, The tests were interrupted periodically and the test
pieces, cooled to room temperature, were examined for total
elongation, the number of grain boundaries and slip lines on.the
gauge length and the magnitude of displacement of both the grain
boundaries and the slip lines. The results are reproduced
Card 2/ 9

24478
S/126/61/011/006/004/011
The effect of substructure F,193/E4183
graphically. (Unless otherwise stated, the number ascribed to
curves,in the diagrams Iquoted,below denote the degree (6,%) of the
preliminary plastic deformation of:the creep test Pieces.)
The general,characte*r of creep of the various test pieces is'shown
in Fig.1, where the elongation W is plotted against time (hours).
It will be seen that with increasing degree of preliminary
deformation the rate of creep decreased. Moreover, no transient
stage of creep was observed in specimen s, preliminarily deformed
,to 6,3-@5%. The effect of such structure on that part of
deformation whi.ch is revealed by slip lines is illustrated in Fig.2,
where the number of slip lines per I cm of the gauge length (n,l/cm),
is plotted against time. Here, in every case, n increased
initially and then remained constant at a level which decreased with
increasing 6. In Fig.3, the displacement at the-slip":lines
(Fckili) is plotted against time (hours). The data reproduced,in
Fig.2 and 3 were used to estimate the part played in creep of the,
test pieces studied by coarse,slip; the -results are 'given in.Fig.,
where elongation due to coarse Slip (Eck,%) is plotted.against
time, and in F'19-5 where the ratio Eck/EO45&&@ (ECS" denoting the-
total deformation) is plotted against EOG&M'- The effect of
Card 3/9

24478
S/126/61/011/006/004/01
The effect of substructure E193/E483
substructure, formed as a result of preliminary mechanical and
thermal treatment, on the deformation of creep test pieces due to.
relative movement of the grains is illustrated in Fig.6, where the
the grains P (iL) is plotted against
relative displacement of
_
g
time. In Fig.7, gap P (11) is plot ed against cogakN).
elongation due to coarse slip a
The above data on the tota nd
elongation due to relative movement of the gralas were based on the
results of measurements. The elongation due to fineslip could not
be measured because the fine slip lines could not be observed under
the microscope. However, the elongation due to fine slip E_x Is
given by Ex CC)S-jq - (Eck + c.rp) and the effect of substructure
on this parameter is illustrated in Fig.9, where ex is plotted
against time (hours)i in Fi .10 Xx is plotted against E
9 @ 4
The results obtained were analysed in relation to the results
obtained by other workers and the following conclusions were
reached. (1) The creep properties of nickel are profoundly affected
by preliminary plastic deformation (in tension),followed by
annealing, since not only is the rate of creep reduced but the shape
of the creep curves is altered. The higher the degree of.preliminar
y
Card 4/9

24478
S/126/61/011/006/004/011
.The effect of substructure E193/E'183
deformation, the smaller is the total elongation attained during
creep in any given time. (2) This.effect of preliminary
treatment (resulting in the development of substructure) is
associated with slowing down of the Processes',.,of both coarse and
fine slip in the interior of.the grains.- (3)@, The rela,t,j-ve
displacement of the grains which can be observed I on the surface of..'@
creep test pieces is caused mainly by non-uniform deformation-of--
grains and not by the viscous flow alorg the gra!@-boun-a_
(4) The change of the behaviour of nick-el.during t@@L-ep-brought
L
about by preliminary mechanical and thermal t m-int is a
-A t n
.manifestation of the effectof tbe.resul_ta etwo@,,,. of
dislocations obstructing' slip, which--c-o-nstitutes the-,main
n There are 10
mecha ism of deformation in cre-ap f 44ires, 1 table
and 25 references: 7 Soviet-bloc. and 11 non-Soviet-bl,@'@@. The'
four most recent refe@@andes to English language publi 'tions read
-T.R., Dunn C,G. Acta met. , 'E, 'N@o ,-
as follows: Hibbard I 1956t .3, 3o6;
McLean D., Fax-mer M.H., J'Ytns@l
Dorn J.F. I AS_-M-11956, 255;
Metals, -1956-57, 85, 41; Parcer, E.R., ASM, 1956, 227."
-ASSOCIATION: Institut metallovedeniya i fiziki metallov .',j3NIIChk-
Card 5/9 (Institute of Science and Physics of Metals lj;@@T
f

PHASE I Esmy, EXPLMT@M: SOV51IZ5
BhC,,rya L", 11, To.rly 41@ksandrovich, llo@tor of Pt,ysica =1 @Lth-t!cz; Yak6v
Goln,Ainor; Vera Euxinskiy, Candl-
do to of PhIsici and :%O.omatIco; @i@tor I'Ar;Dylovich Kardtn@k!y; Vludlilav.
lu-Amirvvra Yritiknya, Candidate of phyeles and Kth-t-cZ, Ivauovlch
Doctor of Technicel @-ience@; Y@rly Andreyevich Oaiplya,,; fl4rk D.-eyJovilch Porlkt5,
Candidate -of Tortnical Sclcncoa; Vlhdimir Kolgoyvich Cv.didnt. of Tech-
nical r-lenios; Na= lift4kovich S4niltr, Cart a o of M-I'MM-Ml@Scl-nata; Nadithd,'
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Trofirovna Travina, Candidate or rkvaics and NAhvmatic5; and Lay X@arkovlch Uttvvkly,
Candidate of To chnical Sciancna.
Roate@,%vrrarll,a v fWcbeakom motallovadanii (Radiography in Physi-dul Y.tullogrelshy)
Moscow, F@tallureizdnt, 1961. 368 @p. 5.200 coploa printed.
Spon3zrl Gcaularstvennyy Sovot =M. Toontrallayy
1.0t1tut cho@rav@f metallurgii im. I P. Bardina. Inatitut
Motallavd...Jy. i flzzil'i 14t.23W.
Lt. (Titl. paeo)s Yu. A. BaCarystalcly; Ed. or publishing Pouzot lo.r. barite; Tech.
Ed.r Y..B. Vynshtoyn.
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PURPOSF, This harAL-cok is Intendol for x-ray %vCtX!CIAA3 VOTkInZ in plant Inborn-
tortes of the motallureical and machina-manufaeturing ir4ustry. 1. may also t.
useful to technteal personnel in thq field of applied x-rmy diffraction on.lynts
employed at sclantific,tachnical, and educational institutions.
COMRAGM The hnndtook contAins best: lnrorvj,ti@on of the methods employed An metal-
logr4phy. It consists of four pttti. Part 1 contains doscrIptiono or methods ror
the study of polyerlst.13, Inoluiina tl,@ special features Of th* @Qrk' with oherp-
focused tuboo and ionization countera, prepuration or speciza.", and choice of
radiation ources, filters, comaraa, and g.0metry of the pict@e. Data on the
photomaterIng of x-ray Pictures and on the application or olactrem, diff'raction
techniques to matal sclenzo are alai presented. , Part 11 contains a detailed
d6rcription of stresses and drrormatlen3 in crystals of metal, as well as of now
motho,is for mfavarine tho alto or j@s!ns and areas of coherent amatterine. The
material Alsa contains data art mothMn for stuAyIne the recry4tallization of estate
for dettminine textures. Part III is devoted to x-ray phase analysis to be cerr%PJ
out with the aid of tables included In the appendix. ?art IV deals with x-ray atu.1-
Joe of sttol ttAt has been variously treated by thor=al and
No raroonalities are mentioned. There are 222 rafer6nm4st 199 Skvlet, 55 EnCli.h,
.26 Gorman# and 2 French.
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S/080/63/036/001/026/026
D2o4/D307
AUTHORS- Motsarev, G.V. and Rozenberg, V.R.
TITLE: On the problem of preparing bis(trichloro-
methyl)dichlorosilane
PERIODICikL: Zhurnal prikladnoy khimii, v- 36, no.
1963, 231 232
,TEXT: The present work is communication IV in
the serie3 of papers dealing with the halogenation of al-4phatic
silanes nnd siloxanes. Ris(trichloromethyl)dichlorosilane M
was prepared in h14% yield by passing gaseous C12 into a solution
of 210 F C13C.CH 3S'C'2 in 20 9 C12, at 600C, over 66 hrs, at
6.1 g/hr, using azo-bis-iso-butyronitrile as an initiator.
CC13 Sici3and CCI 3' CHC12siC12 formed.as by-products. Compound I
coiild also be prepared in CC14 (not less than 5 mol %) using uv
irradiation as the initiator, at 20 - 250C, over 66 hrs, at
6.1 Cl I. CC130sici
2/hr. The latter method yielded. 60 % of 3
Card 112

ACCESSION NR- AP4032495 910080/64/037/00'410747/0749
AUTHOR: Motsare'v, G. V. ;_11oze0e R.
TITLE: Thermal decomposition of t richlo romethyltrichlo roe ilane. Communica-
tion, LK
SOURCE: Zhurnal prikladnoy khimii, v. 37, no. 4, 1964, 747-749
TOPIC TAGS: trichloromethyltrichlor,osilane, thermal stability, thermal de-
composition, mono chlo romethylt richlo ro s ilane, dichloromethyltrichlorosilane
ABSTRACT: The thermal stability of the chloro derivatives of methyltrichloro-',
silane was studied. The mono- and dichloromethyltrichlorosilane are complete-
ly stable on boiling,.even in the presence of anhydrous FeC13. Trichlorome..thy14
@richlorosilane readily decomposes on boiling (160-175C) to form a 90% yield
O'@ S' 14 and 1311/46 yield or C2C14- 0
ic rig. art. has- 2 equations.
ASSOCIATION: None
SUBMITTED: 18Mar63 DATE ACQ: llMay.64 ENCL: 00
SUB CODE: GC @NO REF SOV: 002 OTHER: 001
Card I/ I

ACCESSIM NR: AP40325W S/0080/64/037/004/09W/0922
AUTHOR: Motoarev
G. V.; Rozeaberg, V. R.
TITIE; Initiating the chlorination reaction of methylehlorosilanes with
a
cetyleyelohexylaulfonyl peroxide. Communication VT_T in the series.
SOURCE:- Zhurnal prikladnoy kbimji., V. 37j, no. 4j. 1964., 920-922
TOPIC TAGS: chlorination, mathylchlorosl2ane,, acetylcyclohexyloulfonyl peroxide,"-'-''
initiator, chlorination iniator, chloromethyltrichlorosilane, polychloro-
M@thyltrichlorosilane, dimetbyidichlorosilane, polychlorodimethyldichlorosi3Aiae
azobisisobutymnitrile, ultraviolet light
ABSTRACT: The chlorination of methyltrichlorosilane and dimethyldichlorosilwe
iniated by acetylcyc1ohex;yUulfonyl peroxide was investigated. Reaction proceeds
li very low at 24-30C. At 50C with a@CH SiCl *C12 molar ratio of 1:0-3 t i
here it
I I , low 3-
complete conversion of the chlorine naifig I weight part of the,monochlor- to
1.15 parts of polychloromethylsilanes. Reducing the peroxide ratio to 1:0.2
reduces the polychloro derivatiYes to'0.84 parts.,.The initiating action@ipf this
peroxide exeeeda that of azobisisobutyronitrile-and approaches that of ultra-
Card
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