SCIENTIFIC ABSTRACT ROVINSKIY, B.M - ROVINSKIY, B.M.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001445510017-3
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: July 19, 2001
• Sequence Number: 17
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT


'AUTHORS: Rovinskiy, B.M. and Kostyukova, Ye.P. 70-3-3-30/36
.TITLE: A Simple Method for the Precision Determination of the
Lattice Parameters of a Pclycrystalline Substance Without
an Internal Standard Substance (Prostoy bezetalonnyy metod
pretsizionnogo opredelenlya parametrov reshetki poli-
kristallicheskikh veshchestv)
'PERIODICAL: Kristallografiya, 1958., Vol 3, Nr 3, PP 382 - 383
(USSR)
ABSTRACT: For precision back reflection methods, there is some
doubt as to the effective specimen film distance which is not
removed by using a standard substance as the effective pene-
tration depths are unknown. The,ratio of the observed diameters.
of two rings D /D = f(a) where a is the lattice period.
Values of this ;atio of from 1.090 to 1.140 have been already
given (Zh.Tekh.Fiz., 1940, Vol 10, P 525) but insufficiently.
accurately. A is the effective specimen-film distance.
D1/2A = f(a) . A is plotted against a for the two wave-
lengths of the K alpha doublet and the value of a where.
these curves cross is chosen.. If D and D can be measured-
1 2
to 0.01 and A is about 150 mm, then an accuracy of
Cardl/2 0.00003 can be achieved.

?0-3-3-30/36
.A Sinple Method for the Precision Determination of the Lattice
Parameters of a Polyerystalline Substance Without an Internal
Standard Substance
There are 3 figures and 2 Soviet references.
ASSOCIATION: Institut mashinovedeniya AN SSSR
(Institute of Mechanical Engineering,Ac.Sc.USSR)
SUBMITTED: November 13, 195?
Card 2/2

SOV/24-58-4-18/39
AUTHORS Rovinskiy, B.M. and Rybakova, L.M. (Moscow)
TITIE. The Relationship Between Crystal Size and Yield Point
and Metal Hardness (0 zavisimosti predela tekuchesti i
tverdosti metalla ot velichiny blokov)
PERIODICAL: Izvestiya Akademii Nauk SSSR, Otdeleniye Tekhnicheskikh
pp 100 101 (USSR)
Aauk, 1958, Nr 4~
ABSTRACT: A study is made of the effect of size (e) of the crystal
graIns and non-uniformity (n = Ad/d) of the interplanar
distance in the crystal lattice during permanent deformatiorL
on yield point (a.) and Brinell hardness (HB) of
metals. The exDerimental data used in the study have been
taken from an earlier iavestigation by the present authors
and from investigations by other authors, in pa--ticular
Ball (Ref 1) and Hall (Ref 5). The data are for a low-
carbon steel and pure aluminium.
The various data for as and "B are plotted against
'n 1/2 and e-1/2 and the plots are found to be straight
lines. The authors' straight line for as versus
-1/2
Cardl/3 a passes through the origin of the co-ordinate system,
indicating that a s approaches zero as the grain size

SOV/24-58-4-18/39
.The Relationship between Crystal Size and Yield Point and Metal
Hardness
increases. Hall's straightline is criticised for note
passing through the origin and it is suggested that this
line could be made to do so and still pass through the
experimental points. 1/2
The fact that the plot of a VS. I is also a
s
straight line passing through the origin is used to conclude.
that eTI = const. Doubts are expressed regarding the
validity of the general view that the development of non-
uniformity~of lattice parameters during plastic deformation
of metal is caused by the development of micro-stresses.
It is further argued that Hall's view that the mosaic
structure of grains is not affected by their size-is
incorrect. . -1/2 1 1/2
The plots of H vs. 9, and H vs. 71 are
B B
straight lines intersecting the axis of ordinates at a
Point H_B(O) above the origin. From the various curves
Card2i/3 a relationship is derived for HB and as

SOV/24-58-4-18/39
-The Relationship Between Crystal Size and Yield Point and Metal
Hardness
H H
B B(O) + CaS
where C = el/2 T1 1/2 k and k is a constant depending on
Units,.
There are 1 figure and 7 references, 1 of,which is
Soviet and 6 English.
ASSOCIATION: Institut mashinovedeniya AN SSSR (Institute of
Meehan-Leal Engineering of the Ac.Sc.USSR)
SUBMITTED: January 20, 1958
Card 3/3

'30-1/120-58-5-31/32
1 7 7 7 1
a U 7 G Roviinskiy, B. T.I.
T
13_`:-werition O-L uhe~ if y--Small A~-,ertures Obtained
I),. - za-Plyvaniya
Fir-:TiL-,- -e~allic Fo (Predlokhraneniye ou
_L , Id ils
.re-37---La mialykdi otuverstiy, j;oluchayeuiyIdi prolicalivanijem
1~h f o1'-)
11 i -_ he
-DT P2ibory i te' hni' a eksperim nta, 1958, ITr 57 109 (USSR)
au, -_,ors have descr-Lbed a metIlod for pre L
_pari 1~- Very
-%pcrtu_-es for shadow X-ray raicrosco~,;)y, usin- a cariara
in viaich the
.-C-dra, (Ref 3). Usin:: the PiIT-~; instrument,
L
TI -or
dent. --as re.. -1ced by an electrolytically sharpened
1
or ~',-un-sben needIc:: the end point of -aii-Ich consisted of
._~-Dnq an angle of 10-150 and an end poin'u- curvature
ID
:)f 0.1 ~L, it V,as rj,-.)ssible to pre-pare apertures 0.6-0.8 11 in
t1ji- 7-.
J n a -31d foil 20 11. C Houever, experiments
31-~O`Wn C, aa' such vrarj siaall apertures produced in
U
1 4 . v iz~ 17 30f t do nob I-asu very lon-. After L-wo U'o
-L-rE. A-0-Irs nac:r tend to "fill un" wid durin- this process
an _u
r f o r d becomes either elliDtical,
-,!)re co-.!.-,lic&'ed, Ine f orm, of the aperture is appar
1 G 0 ZT -h- of tAe crystualliue in

SOV/120- 5:-~ -5-31/32
-~n of tLE., Blocking of Very Small Apertures Obtaiaed by
D
Fails
LI i~
r to -Dre-Trent tHe
w1iJoh the apartures are produced. In orde
fillin- up of such a saall aperture a T)late with
a fres-'aly made aDerture was soaked in a very diiuted solut-
i3n of celluLD_id in acetone and -was then dried in air. In
-I's vray a celluloid wall is produced across -th
e aperture
"I preven edure
and tl,.is ts the filling up process. This -Droc
lea's to ape-tures w1nich albhou:3h covered by celiuloid are
'he-, -ra,
L
i e vu- r ess 'u risparent to visible light and X-rays and
i-o nroserve ,caeir ori-inal circular form. Such a--)er-',-LL-_es
re,- noi; aui"4,;-able for elec-.~ron bea:,.is. There are no fi-mres
u. roferences, of which 2 are 3ovi-3-", 1 is Enn-lish.
U
Institut mashinovedeniya AN SSS"R (Irstitutue of Lllechani_
cal E-a-ineerii-11, of ti-ic Acade-ay of Scie~ices, USSR)
November 13, 1957.

SOV/126-6-5-17/43
AUTHORS: Rybakova, L. LT. and Rovinskiy, B. M.
TITLE: Structural Changes in Metals DuriH~-Very Small Rates of
Deformation (0 strukturnvkh izmeneniyakh v metuallakh, pri
ochen' malykh skorostyakh deformirovaniya)
PERIODICAL: Fizika Metallov i Iletallovedeniye, 1958, Vol 6,
1qr 5, PP 8?4 - 878 (USSR)
ABSTRACT: The difference between structural changes taking place
during creep and those due to deformation in tensile
tests is quantitative in nature. Work done in the pas+-
V
on the change in structure in relation to rate of defor-
mation includes electron microscopic investigations of
slip lines in monocrystals of aluminium. eeformed at
different rates (Ref 2).r Polycrystalline material was
investigated by Pashkov (Ref 3). An X-ray investigation
of the influence of the rate of deformation has been
carried out by Braudenberger (Ref 4). Daviden-kov ',Ref 5)
irciestigated the structural changes in steel and coppez
specimens which had been statically and dynamically
compressed. All these investigations, however, are
concerned only with static and dynamic deformation. only
Cardl/3 recently has the influence of a deformation rate 40 to

SOV/126-6-5-17/43
Structural- Changes in Metals During Very Small Rates of Deformation
50 times less than.static been investigated (Ref The
results of this investigation do not agree with the known
experlmentu 'he
al facts. In Figures 1 and 2 the change a' t
half--length.of the interference line for Steel _'10 araeff.
Ni in relation to the extertof total deformation at normal
and -vrery low deformation. rates is shown by crosses and
poirts, respectively. In Figures 3 and 4, four sets of
X-ray photographs are shown, two for Steel 40 and We _-"or
Ni of specimens deformed in accordance -with the stz-ain-
curves of Figures 1 and 2 (i.e. at normal and slo-w rates
of deformation). Whereas, in undeformed specimens the ve
iaterference spots appear clearly definal wit-h proGressi
deformation -they become diffuse, the diffuseness iAcreasing
~b
more rapidly with normal rates of deformation thar. w;- h
slow rates. The lower degree of diffuseness obtained with
slow deformation is due to relaxations of micro-stresses
within the grains accompanying slow deformation and is
broughtabout by mutual displacement of grains or grain
fragments. Such displacement has been observed in plastic-
Card2/3 deformation as well as in creep (Ref 8). In order to
elucidate this phenomenon more fully, a microscopic

SOV/126-6-5-17/43
Structural Changes in Metals During Very Small Rates of Deformation
,investigation using the scratch method was carried out
in which the specimens were scratched in a direction
perpendicular to that of deformation. Micro-photographs
of slowly deformed specimens showed scratch fractures in
the grain boundaries and slip lines in grain bodies more
clearly than those of rapidly deformed ones, thus confirming
earlier reports of displacement of grains and grain L
fractures. There are 4 figures and 9 references, 7 of
which are Soviet and 2 German.
ASSOCIATION: Institut mashinovedeniya AN SSSR
(Institute of Machine Theory of the Ac.Sc.USSR)
SUBMITTED:~ February 18, 1957
Card 3/3

7(6)
AUTHORS; Rovinskiy, B, W., Sinajck_Jiy, V...'!.

TITLE:
Preoaration of the Plot "Lo, -Defornation of the Crystal
ad
Lattice" by the 'Method of Continuous Re~istration
(Polucheniye diaEramm "na-ruzka-deformatsiya kristualliches-
koy reshetkill metodom nepreryvnoy re~istratsii)
PERIODICAL: Zavodskaya Laboratoriya, 1958, Vol 211r, ITr 11,
pp 1367 - 1370 (USSR)
ABSTRACT: In.contrast to the usual method, by which the
defoviation of the sampled. takes place stepivise
and vith each chan,_,,,'e of Uie loa4 the sample is
X-rayed t-le method reported here employs,continuous
X-rayinE on a movinj film. The corresponding defor~-~,,in6~*
load is recorded simultaneously and UUtWatically
on tae X-rany fi'lrii. T'he film holt!er with its film is
turned by tvio SD,-2 synchronous motors. The steel case
with the film _older is attached to the columns of the
IM -12A machine, to which the X-ray tube is also
conveyed (Diaraam, Figure). 'Whicn a BSVL ' tube is used
Card 113 an e_xposure time of.aluout one hour is needed.

Preparation of the flot "Load-Def or.,7at ion of the S I) V; 5 2 - 2 41 i -
Crystal L-5;-,tice" '-1Y the i-ethod of Ccn-ui_ru-o,:s
Correspondingly, t,-,e velocity at 1,11"ich the fi lm-
turns and the velocity of deformation must be
re~,ulated to this period. From an X-ray picture of a
finely granulated, cylindrical (diameter 1)_ mm) dur-
aluminum sample -which had been distended 0,3% and of
layersof lines (511)(333) in the absorption of the
KOL radiation of.copper it is apparent that on the
two symmetrical fields of the X-ray.pla-te the K K
a4 cx .2
doublet forms two curves which can be divided into
four parts. The first section corresponds to the
condition of the load, the second to the elastic
distension, the third to the transition of the de-
formation into the plastic region, and the fourth
part to.-t-he decomposition of the sample. In this last
section the lattice Parameter shows a Jrea-LeT value
than in the initial ccndition, rhich points to a residual
deformation of inverse sign. Amon,-,, the advantages of the
method described is t?-e possibility to observe single
Card 2/3 crystals by X-raiing coarsely crystalline samples.

0 kj
24(6) PHASE I BOOK EXPWITATION SOV/2385
Akademiya nauk SSSR
Nekotoryye problemy prochnosti t-verdogo txela; sbornik statey (Some Problems
in the Strength of Solids; Collection of Articles) Moscov, Izd-vo AN SSSR.,
1959. 386 P. Erratz slip inBerted. 2,000 copies printed.
Ed. of niblishing Hout3e: V. 1. Averly&nov; TLzch. Ed.: R. S. Fevzuer;
Editorial Board: A.F. Ioffe. Academlcian; G, V. Kurdyumov, Academician;
S. N. 71iurkov, Correspond-Ing ~bm"~er, USSR Academy of Sciences; I. P.
Konstantinov, Correqpcading Menfoex, USSR Academy of Sciences; F. F. Vitman.
Doctor of Physical and W-theme:1,ical Sciences, P_-3fessoz (Resp. Ed. ); L. A.
Glikman, Doctor of Technical Sc;ienres, Professor, N. A. Zl&.in, Doctor of
Physical and Mathematical Sniences; V. A. Stepfx0'v,7 Doctor of TL-chnical
Sciences;. Ya.B. Fridmex., Doc"Or of 9~!chnical Scien(!es, Prcfessor; B. S. Ioffe,
Candtdate of Te chuical Science s (Depwt y Re sp. Ed.
PURPOSE: 7his book is intended for construction engineers, technologists, physic-
ists and other persons interested ' In the strerigt~h of materials.
by the Otdeleniye fiziko-
COVERAGE: This collection of articles was co=i1ed
matematiclieskikh nauk AN SSSR(Department of Physical and Mathematical Sciences)
and the Fiziko-t4fmJcheskily institut AN SSSR (Tustitut-e of Applied Physics,,
Card 1/10

Some Problems in the Strength (Cont. Mr/2385
Academy of Sciences, MR) in commemoration of the 80th birthday of Nikolay
flikolayevich DELvidenkov, MBmber of the Uk-ranian Academy of Sciences, founder
and head of t-he Otdel prDchnosti materialov (Depaz-~ment of the Strength of
Materials)at the Institutue of Applied Physics., Academy of Sciences, USSR.
kulltet fizicheskogo mt 41 "1
foulider of the- Fa- -.-tallovedeniya (Department of Phys Cal
Metn_llurgy) a:t -the Leningradskiy polite-khnicheskiy institirl. (Leningrad IPoly-
technic Institite), recipient of the Stalin Prize (1943), the Order of the
Red Banner of Labor (1945) and the Grder of Lenin (1953). , The articles deal
with the strength rf materials, phenomena of imperfect elasticity temper
brittleness, hydrogen embrittlement, cold brittleness, influence of deform-
at-ion speed an the mechanical properties of materials, fatigue of metals, and
general problems of the strength, pla3ticity, and mechanical properties of
nonmetals. Ntunercua personalities azn-, mentioned in the introductory profile
~of Frofe article.
ssor Davidenkov. References a-re given at the end of each
TA5LE OF CONTENTS:
Nikolay Nikolayevich Davidenkov (on his 80th Birthday) 5
Vasillyev, D. M. (Politekhnicheskiy institut imeni M. I. Kalinina,
Le-ningrad-Polytechnic Institute imeni M. I. Kalinin, Leningrad). Na-
ture of the Bauschinger Effect 37
Card 2/jo

EIT ROVINSKIY. B.M. (Moskva)
~,APNIW. G.N. (M,)-ikra. PrUITADDVA, T_A. (Moskw
11 e entifriction
n5,- n sf' 1 changc!~ in grap. it
-,-tci to. fni-tion.. Izv,*N Sl~';R, YL-kh. i mashinostr.
UE), A
S
(KIRA 17:4)
1'7co--184 jl-htz
mashl.-.161.1edanlya AN SSSIR~

ROVINSKIY B.M. LYUTTSNU, V.G. and AVI)vYL-,IIKO, A.I.
Lure
,!11i (sic) Point X-Ray Sources for Point Projection Microscoopy and
Diffraction Examinations,
A paper presented at Second International Symposium on X-Ray Microanalysis
Stockholm 13-18 Jun 59/Soviet Interest in New Techniques for Measuring Density
of Ultra Soft X-Rays in Outer Spape.
SO; B 3,136,o88 31 Jul '59

SOV/180-59-1-3 0/29
AUTHORS; Kostyukova, Ye.P., and Rovinskiy, B.M. (Moscow)
TITLE: Change in the Substructure of Cold-Deformed Aluminium in
Annealing (Izmenen-iye substr~aktury kholodno-deformirovan-
nogo alyumini.ya prJJ otzhige)
PERIODICAL: Izvestiya Akademii Nauk, SSSR, Otdeleniye tekhnicheskikh
nauk) Metallu-.giya i toplivo, 1959, Nr 1, pp 55-59 (USSR)
ABSTRACT: On annealing the structure of a deformed metal changes from
a thermodynamically unstable to a stable state in two
ways: by recrystallization in situ (Refs 1 and 2) or by
primary recrystallization (Refs 2 and 3). The authors
describe their investigation of substructural changes in.
99.99% pure aluminium, A back-reflection X-ray method
was used. with a beam from a broad focal spot passed
through ~ ve.ry narrow cross-shapad diaphragm. With such
diaphragms interfereno.-a spots from perfect crystals are
cruciformi from impe:rfact crystals complex spots are
obtained whose nat-ure and dimensions depend on their
substructure, Tha distribution of spots is shown
schematically in Fig 1. Plate spec-;imens were cut from an
,Card 1/3 ingot., annealed at 3500C for two hours and rolled to 5,
15 and 30% deformation, Fig 2 shows the patterns

-z9-1-10/29
Change in the Substructure of Gold-Deformed Aluminium in Annealing
obtained after a Iealing tha deformed specimens for two
n'
hours at 250, 300, .350.~ 400, 500 and 600OC: the lower
the deformat.i.en the higher the temperature to which the
continuous-line ba!:,k.gTound persists,, Fig 3 gives a more
complete picture (magrifieatjLon X 2), showing differences
in theapot shapes at a given temperature and different
deformations and tLe (,,,hanges I'hat occur as the temperature,
is increased, In this figuresome vertically-extended
spots are visible and to eiuc--.;Ldate their origin the
~authors obtained pattains froin specimens rotated through
900 (rolling direoti,.~,n horizontal). This gave spots
extended horizolftally and the authors conclude that
extended spots are due. to crystallites in which
reorys tall ~.zatioa 4L--, situ has orxurred. They consider
that suf--,h recrys~-allization is the primary and main proces.s
even at', the highast annealing temperature. True primary
Or-ystallization becomes appreciable only with increasing
deformation, It rroduc,~qs perfect crystals whose
Card V3 s4'ructupal nattlar-3 changes w-i.th inczeasing annealing
e-'
tempe7r,atuk-:i~, Fig L. shows an interference spot from a

SOV/180-59-1-10/29 ling
Change in the Substructure of Cold-Deformed Aluminium in Annea
single specimen SUCCeSSively annealed at 250, 3507 40015
500 and 6000C) the increasing angular width of the spot
being associated with the.increasing number of sub-grains
composing the crystallite.
Card 3/3 There are 4 figures anti 6 referencesq 3 of which are
Soviet and 3 English,
,SUBMITTED: August 159 1958

SOV/180-59-2-10/34
AUTHORS: Gallperin, M.Ya.,,KostTakoval Ye.P., and Rovinskiyj B.M.
(Moscow)
TITLE: Change in the Substructure of Metals in Repeated Cyclic
Loading (Izmeneniye substruktury metallov pri mnoookrat-
nom tsiklicheskom nagruzhenii)
PERIODICAL: Izvestiya Akademii Nauk SSSRI Otdeleniye telchnickeskilch
nauk7 Metallurgiya i toplivo,,1959, Nr 2; pp 56-61 (USSR)
ABSTRACT: Increasing attention has been given recently to the
Substructure of crystal- grains. Roviiiskiy and Rybakova
(Ref 5) and others (Ref 4).have shown that the yield-
point strength and hardness increase with decreasing'
sub-grain size. The p-resent work deals with substructural
changes in 99.99% pure aluminium and'electrolytic, nickel
during repeated cyclic loading at '45 cycles/second on a
type MUP-150 machine. Fig 1 shows the form of the test
pieces. kluminium. test pieces were annealed for two
hours at 450 - 500 or 600 OC to obtain weakly- or
strongly-developed substructures, respect-lively. Nickel
test pieces were vacuum annealed for two hours at 9000C.
The strain during tests was determined with a type
Card.1/3 EIDU-IMASh meter with the aid of wire strain gauges glued,

SOV/180-59-2-10/31+
Chan--e in the Substructure of Metals in Repeated Cyclic Loading
to the specimen. The substructure was studied by the
X-ray back-reflection method using a type BSV-I tube
with a copper anode and linear focus (Fig 2). Figs 3
7 give patterns obtained after various numbers of cycles
(up to 10). Figs 3 and 7 related to aluminium
previously annealed at L~50 OC,tested under repeated and
variable sign bending, respectively, and stresses of
1.55 and 1.75 kg/mm2, respectively, Figs-4.and 6 related
to the repeated bending at stresses of 1.15 and 1.75
kg/mm2, respectively, of aluminium previously annealed
at 6oo oc2 and Fig 5 to that of aluminium. at a stress of
1.75 kg/mm2, previously annealed at 500 OC. The
mechanical properties of aluminium with weakly- and
strongly-developed substructures were compared: the
results showed the superiority of the latter material.
The work showed that in cyclic deformation the grain
Substructure of both aluminium. and nickel became more
complicated, this occurring in the early stages and
Card 2/3 ceasing after a definite number of cycles. The changes
which occur in cyclically loaded aluminium depend on the
nature of the substructure in the original grain; the

SOV/180-59-2-10/-'4
Change in the Substructure of Metals in Repeated Cyclic Loading
-this is, the greater are the changes..
less pronounced C~
There is a definite relation between the hardening of
the specimen in the initial stage of cyclic deformation
and.the development of its substructure. Substructural
changes do lead directly to fatigue failure.
There are 7 figures and 14 references, L~ of which are
Soviet, 9 English and 1 German.
ASSOCIATION: Institut Mashi-novedfaniya All SSSR (Machinery Institute
of the AS USSR)
SUBMITTED: March 15, 1958
Card 3/3

SOV/180-59-11-Vi/48
-AUTHORSg Gallperin, M.Ya., Kostyukova, Ye.P. and RovinskiV,_A__b1_-_
(Moscow) ------

TITLE- The Influence of Cvc-lic Loadin on the Structure of
Deformed Pure Metals
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Metallurgiya i toplivo. 1959, Nr 4, pp 82-87 (USSR)
ABSTRACT; X-ray studies of structural changes occurring in 99.99%
aluminiuml:6nd electrolytic nickel'Alere carried out.
Samples were annealed preliminarily deformed to 1. 2 or
4510 and subjected to cyclic stressing by bending. X-ray
pictures are shown for the annealed sample, the sample
after deforming and the sample after various numbers of
cycles in Fig 2, 3, 4 and 5 for alumin3-uni and Fig 7 for
nickel. The annealed sampleg of both aluminium and nickel
give sharp interference spots corresponding to simple
structures with fairly perfect crystallites, After the
preliminary deformation the spots are more diffuse because
there are subgraIns p-resent and the subgrains themselves
are not perfect. The behaviour of nickel under
subsequent cyclic loading; is different from that of
Card 1/2
- ---- -- aluminium. For aluminium the sharpness of thespots
------

SOV/100-59-4-14/48
,The Influence of Cyclic Loading on the Structure of Deformed Pure
Metals
reappears. This restoration is greater, the greater the
amplitude of the stresses and the smaller the
preliminary deformation. No restoration is observed in
the X-ray picture of nickel. It is thought that the
difference in behaviour occurs because aluminium has a
low temper-atux-e of x-eevystallization. The increase in
perfection of the subgrains is thought to be a thermal
process causing recrystallization "in situ1F to take place.
There are 7 figures and 10 references, 3 of which are
Soviet, 6 English and I German.
SUBMITTED. April 23, 1959
Card 2/2

SOV/126-7-1-11/28
AUTHORS: Rovinskiy, B.M., Samoylov., A.!. and, Rovenskiy, G.M.
TITLE.- Crystal Lattice Distortions In Nickel-Based Alloys at
Temperatures of 20-5000C (Iskazheniya kristallicheskoy
reshetki v splavakh na nikelevoy osnove pri temperaturakh
20-5000)
PERIODICAL.- Fizika Metallov I Metallovedeniye, 19,59, Vol 7, Nr 1,
pp 79-90 (USSR)
ABSTRACT~, The authors used samples of pure electrolytic nickel and
nickel alloyed with aluminium, chromium, cobalt and iron.
The composition of these alloys is given in Table 1. The
alloys were prepared in an induction furnace filled with an
inert gas. Thq melts were subjected to homogenising
annealing and were hot-forged. After forging they were-
again annealed at 9000C and then cold-forged in three
mutually perpendicular directions in order to decrease the
dimensions of crystal grains., After cutting into plane-
parallel plates, the samples were avin annealed at temperatures
gradually increasing to 5500C (50 0 hi8her than the
temperatures later employed in X-ray studies). The crystal
Card 1/3 lattice distortions were studied by X-ray reflection at

-B SOV/126-7-1-11/28
Crystal Lattice Distortions In Rickel ased A'loys at Temperatures
of 20-5000C
0
temperatures of 20, 200, 350 and 500 G. A KROS-1 camera
with an exposure :3tandard (Fig.1) was used. Relative
integral intensities of reflections from (331) and (420)
planes were found using a microphotometer MF-4. The
lattice constant of nickel and nickel alloys in the region
20-5000C was determindd to within 0.001 The
relative hardness of nickel and its alloys was Also measured
between 20 and 5000C (Fig.8). The results obtained are
shown in graphs (Figs-2-11) and tables (2-4). On addition
of up to 12.4 at. % of A!, 24.0 at. of Cr, 10.4 at.
of Co and 6.7 at. % of Fe, the distortion of the nickel
lattice was found to be proportional to the amount of the
alloying element present. At room temperature the distortion.
is greatest on addition of' aluminium, and least on addition of',
chromium. At 5001C the greatest distortion is still
produced by aluminium., but the least distortion is obtained
on addition of cobalt. The dependence of the characteristic
temperature of alloys on the amounts of alloying elements
Card 2/3 is shown in Fig-5. It was found that the characteristic

SOV/126-7-1-11/28
Crystal Lattice Distortions in Nickel-Based Alloys at Temperatures
Of 20-5000C
temperature of alloys cannot be obtained by simple addition
of the characteristio, temperatures of their components.
The state of the lattice at the absolute zero is discussed.
It was found that thq Itzerloll energy in alloys depends on
the amount of the admixture and the nature of the alloying
element. There are ll,figures, 4 tables and 12.references,
of which.10 are Soviet, I English and 1 a translation from
English into Russian.
ASSOCIATION: All-Union Scientific Research Institute for Aircraft
Materials (VaesoraznY7 nauchno-issledovatel'skiy Institut
aviatsionnykh materialor)
SUBMITTED: October 28, 1957
Card 3/3

9(6) SOV/48-23-5-3/31
AjTHORS: Rov-,nskiy, B. M., Lyuttsau, V. G., Avdeyenko, A. I.
TITLE: X-ray Shadow Microscopy (Rentgenovskaya tenevaya mikroskopiya)
PERIODICAL: Izvestiya Akademii nauk SSSR. Seriya fizicheskaya, 1959,
Vol 23, Nr 5, pp 545 - 551 (USH)
ABSTRACT In the first part of the present paper the authors discuss
the methods of prepari-ng X-ray silhouettes. Four graphs
serve as a basis (Pig 1). The first of the methods dealt,.,-
with here is the "contact method", in which the X-ray film
is in contact with the sample under investigation. The re-
solving power attains here a maximum of 1L The second method
is the one introduced by Cosslett and Ni=, in which , as is,
known, an electron beam is focused by means of electromagnetic
lenses onto the anode, and from which the X-rays then depart.
The resolving power attains here 0.1 to 0.2p,.The third
method is the one described by the authors, which consists
essentially of.a tapered anode as point source of the X-rays..
A resolving power up to 0 ,6& is attained therewith. The
last method described goes under the name of camera obscura.
Card 1/3 Here, the X-ray light originating from an areal source enters

X-ray Shadow Microscopy SOV/46-23-5-3/31
a chamber, containing sample and film, through a small stop.
By this method the authors attained a resolving power below
1 In the years 1952 - 1953 the authors worked in the
aSh AS USSR on the development of X-ray shadow microscopes.
1
It is pjinted out that this type cannot cope with the re-
solving power offered by electron microscopes. A new model
is described in the second part of this paper, complying with
the third principle described above. A graphic section is
shown and details are discussed. The maximum magnification
made possible by this instrument, is 650fold; the negatives,
however, may be magnified photographically up to 2000fold.
The resolving power attains from 0.2 to 0.5,%v . For an
exemplification, two pictures of a net are shown, the first
of which exhibits a 400fold magnification, and the second,
by photographic methods, a 2000 fold magnification. The final.
part of the paper is devoted to the range of applicability
of these microscopes; in this connection two pictures are
shown depicting mineral samples, one of an insect preparation,
two of histological preparations, and two pictures of metallic
alloys. The conditions are specified under which each of
Card 2/3

05739
28(5) SOV32-?5-10-28/63
AUTHOR; Rovinslsl_7 Professor, Doctor of Physical and Mathematical
Sciences
TITLE: The Problem of the C1 "sih-b'atibn aril Ma.nifesi;~~m f Residual
Stresses. (Answers to the Article by Aei~demician N. N. Davidenkov
Publinhod In Ni- 3 of the Periodical for 1959 Have Arrived at the
"Zavodskaya Laboratoriyall.
Editorial Office of Wic Periodical
These Answers Are Given Below in the Form of a Discus8ion). 111.
PERIODICAL: Zavodskaya laboratoriya, 1959, Vol 25, Nr 101 pp 1228-1230
(USSR)
ABSTRACT:
The author points out that N.N. Davidenkov's (Ref 1) division
of residual stresses into three classes is inaccurate and
~incomplete (Ref 2), and that the third class having no physical
sense is to be excluded from any classification of stresses. It
is pointed out that the stresses in state of equilibrium in the
macrovolume cannotobe specified except for by the general
classification of stresses (Ref 3), and the terminology of the
Komissiya p0 tekhnicheskoy terminologii AN SSSR (commission for
Technical Terminology of the AS USSR), and can be termed
Card 1/2 I'macrostresses" only in some cases., The stresses of "second clasd'.

o5739
The Problem of the Classification -and-tManitfestation, of sov/32-25-10-28/63
Residual Stresses.(Answors to the Article by Academician N.N. Davidenkov
Published in Nr 3 of the Periodical for 1959 Have Arrived at the Editorial
Office of the Periodical,"Zavodskaya Laboratoriyall. These Answers Are Given
Below in the Form of a Discussion). III.
should be better termed I'microstresses" or crystallite stresses".
The "stresses" in state of equilibrium in submicrovolumes should
be termed "lattice deformations". Terms like "deformations of
3rd class" and "deformations of 2nd class" should be avoided
since they are not scientifically founded. In an X-ray
visualization of stresses, the appearance of a line shifting
should really not be applied to the classification of stresses.
on considering that an extension of X-ray lines also depends on
the size of blocks and other factors, the inexpediency of a stress
classification on the basis of X-ray phenomena becomes even more
evident. As the weakening of the line intensity in (Ref 1) is
referred.to "stresses of 3rd class", it is not dealt with
(for the above-mentioned rep-sons). There are 4,Soviet references.
Card 2//..3

24547
S/179/61/000/002/015/017
g 2 C)o E073/E535
AUTHORS.- Rovinskiy, B.M. and Sinayskiy, V.M. (Moscow)
TITLEt The relation between oriented micro-stresses and
residual irreversible deformation in metals
PERIODICAL: Izvestiya Akademii nauk SSSR, Otdeleniye tekhnicheskikh
nauk, Mekhanika i mashinostroyeniye, 1961, No.2,
pp.146-147
TEXT: The results are described of experimental investigation
of the residual deformation ofthelattice, and consequently*of the
oriented micro-stresses, on the magnitude of residual irreversible
deformation of specimens made of steel 45 in pure compression and
tension. After machining, the specimens were annealed in a
vacuum furnace at 7860C and then deformed by means of the test
machine VIM-1-1A (IM-12A). One series of specimens was subjected
to pure compression, the other to pure tension. The rate of
deformation was 2 mm/min. The residual deformation of the lattice
was measured by X-ray diffraction and is shown graphically as a
function of the residual irreversible deformation of the specimens.
The residual deformation of the lattice is taken as a measure of the
Card 1/2

24547
The relation between oriented S/179/61/000/002/015/017
E073/E535
oriented micro-stresses?, it shows a maximum value at about 1%
residual (plastic) deformation of the specimens. On further
increase of the plastic deformation of the specimens, the residual
deformation of the lattice falls continuously. The oriented
micro-stresses are therefore at a maximum at plastic deformations
of about 1%. Therefore. plastic deformations approaching 1%
should be avoided if oriented micro-stresses have an adverse
~effect. There are 1 figure and 6 references: 3 Soviet and 3 non-
Soviet.
ASSOCIATIONi Institut mashinovedeniya Akademii nauk SSSR
(Institute of Science of Machines. Academy of
Science. USSR)
SUBMITTED: December 9, 1960
,Card 2/2

Mai
5/126/6i/011/002/0l.6/025
E 1. 9,3/E1,83
AUTHORS, Rovinsliiy, 13,111, and Lyuttsau, V.G.
TITLE, Dependence of-the Rol,.-txation Stability of Metals and
Alloys on tht- Atomic 11oncling Forces and Lattice
Distortions, and Correlation of the Relaxation.
a r d
Stability With 11, ness
PERIODICAL,, Fizjka metallov i metallovedeniye, !961, Vol.11, No.2,
PP~285-289
TEXT: It has buen ihwm F-arlier by the present authors (Ref.1-4)
that the relawation of' bo0i the izi-Ltiai stresses a and the
res:Ldual, oriented -i~.resse-s is by the equation
'Exv
kLL
wh e r eCo and C1 derioLe the ).elative elastic deformation of the
material, raeasuredL reipecrivily, on the app.lication of the load
and after time t doring 7which The te.!:t pie-ce deformed
elastically; 1i and p are parameters which characterize the
intens-Lty of the relaxarion pro-:,Esses' kj beLng dependent on the
Card 1/ 3

5/126/61/011/002/oi6/025
Dependence of the Relaxation E19,3/E483
Magnitude of the Stress and 1) clepending on the nature, sty,ucture
and state of the- rllatc,!Ial~ The non-dirriensional parameter ps
to ahicAi e-ariier a term flptasti-~L_ity inde-xll was a5cribed (Ref.1),
appears to be a un.vversal characteristic of the mechanical
properties of metalsi the object of the present work was to
establish tile relationship between p on one side, and the
so-called lattice rigidity coefficient K, the degree of lattice
distortLon and he%r'dtLeiS on the other. To th-is,end. data obtained
earlier by the present authors (Ref`~1-4) on pure metals (Ni. All CU)
and alloys Ru-,Al, Ni-Al, Ni-Cr, Ni.-Fe. Ni-Cu), tested between
1.8 and 400-~C ware analysed, Since p J.n Eq.(1) varies between
0 and .1 R ...' O./p) .. I(Vary:Lng between 0 and W was taken.as
the wea-iurp at the relaxation stability in the present work. The
followi.n,g conclLisi,-,ns were reached, (1) The relaxatlon stability
R of pure meLils varxes linearly with K2; this law, however,
does not apply to alloys, (2) The relationship between R and
Brinell hardness nu;Ajer is aLso Linear4 (3) The increase in the
relaxation stability and hardness of alloys is brought about by
static lattire distortions, caused by the Introduction of the
alloying elerients atoms, (4) The decrease in the relaxation
Card 2/3

S/126/61/oll/oo2/016/025
Dependence of the Relaxa-"Ion E193/E483
stability and hardnes.-i of pure metals at elevated temperatures is
caused by an Increase -in the intensity of the thermal vibrations of
atoms in the lattice, There are 5 figures and *7 Soviet references.
ASSOCIATION: Institut mashinovedcaive AN SSSR
(Instirute of Science of Machines AS USSR)
SUBMITTED,.; July 26, ig6o
Card 3/3

L-2-4471-66 EWT (ra 04P (W)NEVIP (t
'ACC NR:* AT6010574 (N) SOURCE CODE: UR/060O/65/000/000/0054/0063-e
Rybakova, L. H.; Herenkova, R. P.; Rovinskiy, B. mi,
7f.
ORG: State Scientific Research Institute of the Scienpe of-Ma!abifleg,(Gosudarst-
vennyy nauchno-issledovatellskiy institut mashinovedeniya)
%%Q0
',,''TITLE: Electron microscopic and metallograiphic analysis of the nature of structural
fractures during cyclic deformation.
:..:.'',SOURCE: AN UkrSSR. Mekhanizm plasticheskoy deformatsii,metallov (Mechanism, of the
~.-plastic deformation of metals). Kiev, Naukova dumka, 1965, 54-63
F-7
TOPIC TAGS: copper, iron, cyclic teBt, material deformation
A.-
-ABSTRACT: The authors study the kinetics of structural changes which take place
-iwithin a metal subjectedto cyclic deformation.. Electron and optical microscopes
Armco~iron specimens were c er-
:were used for the-study. Copper and studied. The
ispecimens were subjected to pulsating cyclic deformation4ith a,constant deformation -V.",
~amplitude of 1%. The specimens were tested to complete fracture'-(600 cycles) ands
'to a given number of cycles (1, 2, 3, 10, 50, 150 and 400Yat a loading frequency.. of
!12 cycles per minute., The, iron 'specimens were tested by a,method described in
'Card 1/2
7,

Pinsher ("Basis of difftactional
by
-6`. -a 13
methods of investigation o~ per-:'6 crys U
Royin3lcj bakova pinvestigation of de"6ndenoe
y and L. I, - Rv
5-T properties on characteristics of structure
of motalsll-), Usilcov ("Application
gkiy and F. M.,
of microscopy in investigation of structure of alloys"),
A. A. 'Dradvoditelev and N. TvaDunina ("Role of repro-
duction of-d--ZIi1--oca--t-ions in process of plastic flow"), A. V.
pe~-
.LT. V.
.tSOV,
_.-Pertsov and E. D. Slaukin. "Self -producin'S
dispersion of metals under action of strongly
zu-nerficially-active metallic, Melting".) and I. L. Mirkin
("Prob'ams of structural investigations adfanoe -Iry-
requirements of p.-ogress of technologyn
re7orts presented at the 3rd Intervuz Conference on Strength and Ductility of
Metals, Petrozavodsk State University, 24-29 June 1963.
(reDorted in Fizika Metallov i Metallovedeniye, Vol. 16, No. 4., 1963, p 64o.
JPRS 24,651' 19 May 1964.

LUTSAU) V. G.; ROVINSKIY, B. M.
"the relation between substructure and concentration inhomogeneities in alloys."
report submitted for 6th Gen Assembly, Intl Union of Crystallography, Rome,.
9 Sep 663.
Inst of Machine Sciencesj Moscow.

4#' z 160 816 2 2
3/181/60/002/06/10/050
B122/BO63
.~,IJTHORS- Plavnik, G. M., Rovinskiy, B. M.
TITLEs Invest-igation of the Submicroporosity of Low-absorbing Mater-
ials by the Method of Multiple Small-angle X-Ray ScatteringTI
P_~;RIODICALA Fiz-Lka tverdogo tela, 1960, Voi~, 2, go. 6, pp. 1099 - 1106
TEXT~ By way of introduction, the authors discuss the experimental con-
ditions required for the application of Lambert's and Guinier's simple
Telation for the calculation of the-11radius of inertia" R of the non-
6,1L
homogeneous regions M 0.004 R wL h the qid of multiple small-,
angle scattering (L integral width of the multiple scattering curveg
m mcv3s of the sample per irradiated unit area in g/cm 2, 0 - density of
It was established in this connection Thai. ~he formula is
a-,Ii~abie when using thick samples so as to attain a complete.scat-
tering oil the primary beam in the sample by sufficiently frequent scatter-
i n is facilitated by thp lic-E -f ir-terials with high ssattering power.
Ca

81622
Investigation of the Submicroporosity of Low- S/181/60/002/06/10/050
absorbing Materials by the Method of Multiple B122 B063
Small-angle X-Ray Scattering
Again, high scattering power is secured by the use of materials with
large R. However, a comparison between the results of the usual small-
angle scattering and those by Lambert and Guinier is not 3c easy. In this
connection, the p'a'per under review reports on studies made on nonannealed,
low-absorbing BeO, which exhibits a considerable inner submicroporcsity
(fluctuation of pore size from 20 to 250 A). With a view to simplifying
the determination of L, the authors developed a method allowing the direct
determination of Lfrom the measurement of the scattering intensities
I,, I from two different distances from t'- counter (one being in the im-
mediate vicinity to the counter) (Figs. 1 and 2). The setup described was
connected to a ';'PC-50VI(URS-50I) apparatus. Scattering curves were repeat-
edly drawn of 11 samples with a thickness ranging from 0.06 to 0.80 glCM2
and the curves (L L ) 2 LO/L, (2), and Ic,/Ii (3) were drawn as
0 i integr
furctions--of m (Fig. 4).,In the case of a small m, curves I and 2 were
found to differ from one another. In the case of larger m and prevailing of
multiple scattering, the intensity distribution curve assumes a Gaussian
Card 2/3

Investigation of the Sutmicroporosity of Low- 3/181*160/02/06/10/050
-:pl
absorbing Mat,erials by the Method of Mult.L e B! 22YB06 3
-Small-angle X-Ray Scattering
character, and the tw~) curves run in parallel in their linear part. The
radius R is determined from the,slope of these straight "lines (R - 270 A).
A maximum pore radius of 255 A results from the usual small-angle scatter-
;ng from tlin samples The multiple X-ray small-angle scattering simpli-
fies and facIlitates the determination of the porosity, of a.materiali and
is well applicable for the determination of the radii. R of non-homogeneous
regions larger than 100 A. Comparative data by.S. M. Astrakhantsev and Ya.
S, Umansk y I (the former also supplied the beryllium samples) were
_~._(Ref. 8)
also u3ed to Interpret the results (Table). There are 4 figures,, table,
and 9 referer_-ese 2 Soviet, 2 American, I French.
AISOCIATTON.~ Insti.tut mashlrovedeni-ya AN SSSR, Moskva (Institute '3f
z
Machine Construction of the AS USSR, Moscow)
I'~'I~ED August 31, 191-9

S/03 2/6 3 /02 910011010/022
B104/B186
AUTHORS: Yovins~iy, PA., and.Lyutsau, V. G.
TITLE: X-ray microflaw detection
PERIODICAL: Zavodskaya laboratoriya, v. 29, no. 1, 1963, 38-41
TEXT: Two radiographic methods of detecting flaws-measuring less than
0.1 - 0.2 mm in metals are described. First method: camera obscura (fig.1).
The diameter (2) in the W or Au plate is 0.005 mm, the plate thickness
0.2 mm. The enlargement ranges from 10 to 20. Second method: x-ray
projector (Fig. 2). The electrons coming from' the wire electrode (1) are
concentrated on the tip of the point anode (2) through the electrostatic,- b
lens (3). The x-rays then move oppositely to the direction of the electron
motion. (1) in a loop of a thin W wire. Using the first method, defects,
of a size no greater than 10p can be traced, and using the second method
even defects of 14 can be detected. T-here are 6 figures.
ASSOCIATION: Institut mashinovedeniya
(Institute of the Science of Machines)
card 1/2

000/005/004/03-2
5/179/62/
zIq1/Vj35 (J~joscow)
N
L.'j. tiolls in
and Ilybalcova v e
d_f ornia
ersiblc
cl irrev 8 ions hn3-
lto%f Jn at, 'I . e%t .0t tew 1.9629
jolts I the stresses dc 1e ni-Y e no. 5
tile e S t 3-ya' ervi.)re
On metals JZV
-IT LF, cluc sc;p,. ashinostrp
naux 5 - I i
Iadetnila 'J~chani:kcaL. -Cal re,
1, _ndr3
Clally Pu
Ilau was ,~de 0" IF, C commer teeli
68-7Lk- IStudY lats O~ rbon between
elita- r1ge d latioll
e)'p er-Im 3.call-f arra iron atid .0- ~t'ne re tion.
St P111 ,,metr 'krr ILICO hithe 'rto 1. on ) defOrlua ter's ileL
C 0. IT w ith S' A'I' NI, tl-,arl b 1e, 0 n a a be
the Specimens led cul data revers-3- . mation tress COUI he
f defO S
U11111 annea, re liable residual lart e 0 the, tr Xle d aga ins t t
vac ore t1le SaIner an
to Obt;0L3.TI -tress a d a tthe .,,,,,Sed that tion hardness
the tr e b I ILIC e al 'ive 'lonsa uslY, d out,
tile t e c0 e we e S relat ..ultlie.0 rr je lotted
wer . e5 a ISO Ca ss is P
Of th e I BI- area.
n1acl t e re Of were stre t i0 r,
5t C. 3-9 atio'n true
e tp rnlil the e l0uga
t tte(l ive Ic- a tive
PI e a a i. ced W herel.11 rela
es i a lie allo r e r 0 re.idual
ar t e .a-8I------
t tests 00t0
e (Z-e, S,vera a ph S ar onail. t 0
and t,6e the Sq" 0 the
Z;a ills ct b e e1'.tcSqual-e
card P, -A I_/3 1 y e1 .

on the stresses and irrevers ible S/179/62/000/005/oo4/oi2
E191/EI35
plastic terni. it is shown that,.from thelinitial values of the
coefficient of plasticity and of the hardness, the limiting values
can be easily obtained. The mechanical condition of a material
can be described by the relative hardness and the relative
plasticity.
There are 7 figures and 2 tables.
SUBMlTTED: IaY 7 962
Card 3/3

S/179/62/000/003/010/015
E191/E435
AUTHORS: Rovinskiy B.M.L-Sinayskiy, V.M, (Moscow)
TITLE: On the effect of the rate of deformation on the
magnitude of the residual oriented microstresses
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye
tekhnicheskikh nauk-. Kekhanika "i mashinostroyeniye,
no.3, 1962, 159-16o
TEXT: The magnitude of oriented microstresses has been previously
related to the equivalent yield stress under reversed loading.
Oriented microstresses have been shown to be mainly responsible for
the reduction of the fatigue strength due to even a small prior
plastic.deformation. Standard cylindrical 0.45% carbon steel
test pieces, prov�ded with precisely machined longitudinal flat
lands, to facilitate X-ray investigation, were examined.
Carefully conducted tests in tensile testing machines covered a
range of plastic deformation between 1.2 and 1.5'1'0 and a range of
rates of deformation up to 30 mm/min. The ma'gnitude or oriented
microst-resses Increases several simes within this range of speeds.
To avoid oriented microstresses, which always have an adverse
Card 1/2

39510
S/123/62/OOO/Oi4/005/020
Aoo4/Alol
AUTFORS: Rovinskiy, B. M., Lyuttsau, V. G., Geveling, N. N.
TITLE: investigation of the relaxation resistance of nickel-base alloys
PERIODICAL: Referativnyy zhurnal, Mashinor~,troyenlye,, no. 114, 19U2, 23, abstract
14A150 (In' collection. "Issled. po zharoprochn. splavam". V. 71
MoscowAN SSSR, 1961, 122 - 128)
TEXT: The authors report on the results of investigating the relaxation of
orlented residual micro-stresses in Ni-base alloys with Cr, Fe, Co and Al addi-
tions at temperatures in the range of from 20 to 4oOoC. The authors measured by
the x-ray diffraction method the residual deformation of tlie'lattice, originating
as a result of tensions exceeding the elasticity limit (5 - 10%) and subsequent un-
loading of the specimens, and also changes in the residual deformations taking
placein the course of time. It is proved that the optimum increase in the re-
laxation resistance of alloys is obtained with Fe, while Cr yields the poorest re-
sults. The relaxation resistance decreases with a temperature increase; this
takes place abruptly in pure Ni and in the least degree in Ni-alloys with 12.4
atomic % Al.
rAb tracter's note; Complete translation]
L s
Card 1/1

S/126/62/013/005/012/031
E073/E535
AUTHORS: Rovinskiy, B.M. and Lyuttsau, V.G.
7 IT,. L: Relaxation of- the hardness of cold-worked metals
~-tjid deppndence of -the hardness on crystal lattice
o 1, tJ, 0 it s
P E R 10 D I Ck 1, Fizika metalk"IV i IlletalJovedeniye, V.13, n0-5. '1962,
724-727
The spontaneous decrease (relixxalaori) fit litirdriems of
cold-worked, 99.990,~' purity, aluminitint Gxt room temperattire) nild
purily c0
pper (at 80'c) was sttid ed. Specimens
20 x 20 x 20 min were machined and heat-treated so its to obtain
u:jif ox,m gr;.jin size. After determining the hardness in the initial
State, the specimens were defortaed by successive compresslon in
three mutually perpendicular directions~until a total reduction
of 50~,,, was reached in each of the directions. Then, the hardness
was again determined both iirwiediatelly and at certain time
intervals up to a total of 5000 hours- During 500 hours the
hardness of alurainium dropped from 39.0 to 29.9 and that of copper
from 80.0 to 66.8 Brinell units. The hardness of the specintens.
Card 1/3

Rol.;7ixation or the hnrdness S/126/62/013/005/012/031
E073/E535
in the initially pnnealed state was 20 and 38 units for- the.
aluminitim and copper, respectively. The obtained hardness
relaxation ctirves are similar to curves of the relaxation of
lattice distortions in cold-worked nietals. The.obtained results
are plotted in graphs, ln(H t/H0 )vs. f(t), where H0 and
Ht - hardness directly and after a time t after cold-working the'
V
metal, respectively. It is assumedthat the hardness
relaxation is caused bytv;osimultaneous, independent processes which
can be expressed by means of the equation
H = H exp k t 6
t 0 H 3/2
a+bt
-.-here ii: speed of hardness relaxation caused by one of the
r)rocoswlles; b and c -constants of the second process (a = 1/0.
For one process,expressed by
k t f(t) and f(t),
H
~./2
11 + bt~
Card 2/3

Rela-,ation of the hardness ... S/126/62/013/005/012/031
E073/E535
the relaxation tii;~es are 940 and 1400 hours for the aluminium
znd copper, respectively. For the second process the hardness
relaxation is virtually complete after 100 hours for both
aluminiura and copper. . Coiaparison of tl
ie relaxation curves of
the hardness and of the residual lattice distortions, determined
from measurin- the, integral Debye line intensity, shows complete
agreement for aluminiurri. For copper agreement is not so good
and this is attributed to differences in measuring conditions
(additional influence of heating and cooling cycles). There are
figures and 1 table.
ASSOCIATION: Institut mmihinovedeniya AN SSS]R
(Institute of Scien'ce of IMachines AS USSR),
SUMMITTED: December 7, 196o /,in�t�a1iy)
December 12, 1961 (after revision)
C:,-. r e

S/699/61/007/000/012/044
Investig-,ting the relaxation D217/D303
exam_ination~.The X-ray method was also used for investigating stir--sT
relaxations~ This consisted of measuring the residual lattice defor-
mation after ex'Lension (or compression) beyond the elastic limit
and subsequent unloading of the specimens,and its change with %imeo
--For this purpose, thespecimens, after being X-rayed; were defor-
in the original unstressed state in a normal tensile testing
machine up to 5 - 110 % elongation which, after Krloadingi g_T~ve the
required residual plastic lattice deformation, [Abstractor7s note,-
'Elastic lattice deformation' in -the original article appears to be
an evror]. The curves for the relaxation of residual orientated mi-
crostresjes in pure nickel and Ni.-Cr, Ni-Al, Ni-Co and Ni-Fe alloys,
obtained by precise lattice period measurements at room temperature
and elevated temperatures,~ can be described by the equation F-t
exp - [kl-c]P, where z0 anId Et = pe--centage macroscopicelastic de-
formation of specimen immediately after loading and after time t,,
respectively; k1 and plare col-stants cha racterf z.-j--g -the intensity
of relaxationg k being determined by the level of stress, and p by
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S/659/61/007/000/012/044
investigating the relaxation ... D217/D303
the nature and state of the material. The value of p characterizes
quantitatively the relaxation resistance of pure nickel and of the
investigated alloys both at room and elevated temperatures. The re-
laxation resistance of alloys is higher than that of the pure metal,:
since it increases with an increase of the alloying element. Addi-
tion ol Fe increases the relaxation resistance of Ni most
ly, and the addition of Or, least effectively,, The relaxationlresi-
stance ol"' Ni and its alloys decreases with increase in temperature,
the decrease being.most drastic in -the case of pure Ni and least
in the case.of a nickel alloy containing 12.4 at.% Al. There are 6
figures and 3 references: 2 Soviet-bloc and 1 non-Soviet.-bloo. The
reference to the BEnglish-language publication reads as follows E.
A. Owen, Y.H. Liu and D.P. Morris, Phil,Mag., 39, 1948.
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30449
S/126/61/012/003/001/021
E021/E180
AUTHORS: ~,ovinsk4,n B.M., and Lyuttsau, V.G.
TITLE., Relaxation of distortions in the lattice of cold
worked metals
PERIODICAL. Fizika metallov i metallovedeniye, v 12, no.3, 101,
305-31.3
TEXT; The spontaneous increase in intensity of Debye lines,
indicating relaxation of distortions in the lattice, was
investigated. Homogeneous fine grained, cubical samples were
prepared from 99.99% aluminium and electrolytic (99.92%) copper.
X-ray photographs showed that the samples possessed no texture.
An X-ray photoxraph was taken of each specimen. The specimens
were then slowly compressed in three mutually perpendicular
directions in several operations, giving a total reduction of
about 5OV.. The hardness.of aluminium and copper increased by a
factor of two, which showed the presence of considerable lattice
distortions. Further X-ray photographs were then taken over a
period of 500 hours. The integral intensities of the (420)
aluminium and (400) copper lines were measured. After deformation,
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Relaxation of distortions in the S/126/61/012/003/001/021
E021/Eift
the intensity of the aluminium line decreased by 45% and that of
the copper line by 41-45%. After a further 500 hours the
intensities of the lines were restored near to their original
values, At the same time the intensity of the background
de'ereased. These results were interpreted as meaning that
lattice defects developed during cold working are healed after a
time and that the distortion is therefore relaxed. The data were
analvsed and it was shown that the curves of relaxation of
d-istort�on could be explained by two -independently occurrIng
processes. The first of these processes takes place at a constant
rate, and is completed in 940 and 1480 hours for aluminium and
copper respectively. The second process takes place intensively
a'. first and then the rate sharply decreases. This process is
almost complete after 100 and 200 hours for aluminium and copper
respectively. Hardness measurements confirmed that relaxation
takes place with time. The results of studies of relaxation by
hardness measurements will be the subject of a separate report.
There are 5 figures and 13 references: 7 Soviet (two of them
Russian translations from non-Soviet publications) and 6 non-Soviet.
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Relaxation of distortions in the 5/126/61/012/003/001/02.1
E 021/E180
The four most recent English language references read as follows:
Ref.l: D. Bowen, R.R. Eggelston and R.H. Kropschot.
J. Appl. Phys., 1952, Vol.23, 6-3o.
Ref-5: B.E. Warr-en and B.L. Averbach.
J. Appl. Phys., 1949, Vol.20, io66;
P.S. Weiss and I.R. Slark.
J. Appl. Phys., 1952, Vol.23, 1379.
D. Michell and E. Lowegrove.
Phil. Mag., 196o, Vol.59 No-53, 499.
Ref-7: F.R.L. Scho-ening and N.I. van Nlekerk.
Acta met., 1955, Vol.3, No.1,10.
Ref.11: M.S. Paterson,
j. Appl. PhYs., 1952, Vol.23, No.8, 805.
ASSOCIATION: Institut mashinovedeniya AN SSSR
(Institute of Science of Machines, AS USSR)
SUBMITTED: January 11, 1961
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28971
S/179/61/000/003/014/016
E073/E535
AUTHORS" Gal'Perin, M.Ya., Rovinsk
I M. and Sinayskiy, V.M.
(Moscow)
TITLE. On the influence of preliminary tensile plastic
deformation on the fatigue strength of steel
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye tekhni-
cheskikh nauk. Mekhanika i,mashinostroyeniye, 1961,
No.3, pp.161-162
TEXT: Most authors mention only an increase in the fatigue
strength as a result of increasing wor k hardening produced by
applying tension. N. 1. Chernyak (Ref,l., "Fatigue strength of
preliminarily stretched steel". Symposium Tr. In-ta stroitel'noy
mekhaniki AN.UkrSSR,,1953) found that a small amount.of plastic
deformation by tension does not increase but lowers the fatigue
of steel. For,J = 1.0-2.6% a minimum fatigue strength is reached,
then the -fatigue strength increases and for J= 12% it reaches
a value corresponding to that of undeformed steel. The work
described in this paper was carriet! out for the purpose of
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28M
On the influence of preliminary S/179/6i/ooo/603/014/016
E073/E535
determining the relation between the magnitude of oriented
residual microstresses occurring during plastic deformation in
tension And the drop in the fatigue limit, Medium carbon steel,
Steel. 45, or 25 mm diameter was used in the tests, the mechanical
chara,~-Aeristics of which were as follows-,
2 2
-1 kg/mm
=.39.8 kg/mm CT 66.U
22.2%, 4.89%, a 9,J kgm/cm 2, H 152
k B
Several batches of specimens, 12 in each batch,, were produced.
The shape ofthe specimens was such that the same specimens could
be used,without further machining,for the fatigue tests. The
gauge length was 22C mm, the 20 mm long central section of which
had a diameter of 8 mm. Fig.l. After machining to the desired
size and surface quality the specimens were annealed in vacuo
at 7800C for two hours and then allowed to cool together with the
furnace., Following that, they were stretched at a rate of
2 mm/min within a range of 0 to 10%,, For the gauge length the
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2 8 9 7 1
On the influence of preliminary S/179/61/000/003/014/oi6
E07-"'/E535
error in mz!asuring the length did not exceed 0,0394. The fat�gue
tests were cavried out with a loading frequency of 3000/min for a
total duration of !of cycles. Prior to the fatigue tests, the
oriented microstresse5 were determined by X-ray methods; two
X-ray diff"raation patterns were taken from the same spot, one
'befcr-3 and one after loading. The obtained results are plotted in
Fig~2 and it can be seen that the maximum drop in the fatigue.
strength was achieved in the range of preliminary deformations of
I to 2%, which is in good agreement. with the results obtained by
Chernyak fcurve 3). The deviation between his results and the
results of the authors of this paper (curve 1) is attributed to
the fact that Chernyak did not anneal his specimens after
machining. Fig.2 also gives the relatiog between the magnitude
of the oriented microstresses (Y (kg/mm ) and the magnitude of
preliminary deformation (curve 21, It can be seen that this
curve has a minimum approximately for the same range of plastic
deformation.as waa observed for curve 1, The curves 1 and 2
show similarity for small plastic deformation:~ the influence of
work hardening start.-5 ~to man'Afes". itself at 2% which leads
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2 7-L
On the -influer--E~ of preliminary s/t7q/61/ooo/oo,,/oi4/oi6
E073/E535
to an increase in the fatigue strength. The obtained results
conf--rm lis assumption of the decisive role of residual
oriented mi--rosiresses on the fatigue strength. This is in good
agreement with da:a published earlier by the authors (Ref.6z
Izv,AN SSSR, 0'rN., tMekhanika i mashino5troveniye, 1961, No.2) on
the relation between oriented microstresses and the residual
plastic deformati.on. However, it is nct as yet possible to
propose a simple mechanical model of 'he phenomenon since the
magnitude of the oriented'microsrresses is much greater than the
drop in the fatigue Limit. There are 2 figures and 6 Soviet
referen--es.,
ASSOCIATION% Institut mash-inovedenlya AN SSSR
(Institute of Machine Science AS USSR)
SUBMITTED.- January !8, 1961
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PHASE I BOOK EYJWITATION SOV/4229
Madorskiy, Yakov Yudovich, and Efraim Vollfovich Rovinskiy
Teoriya aviatsionnykh dvigateley, chast' 1: Oanovy ter7nodinamiki I gazovoy clinamiki
(Theory of Aircraft Engines. Pt. 1: Fundamentals of Thermodynamics and Gas
Dynamics) Moscow, Voyenizdat, 1960. 211 p. No. of copies printed not given.
Ed.: M.S. Pisarev, Engineer-Colonel of Supplies; Tech. Ed., T.F. Myasnikova.
PUTPOSE., This book is intended as a textbook for students at technical aviation
schools. It may also be useful to the flying and technical personnel of the
V7S (Air Forces), GVF (Civil Air Fleet), and DOSAAF (All-Union Voluntary Society
for the Promotion of the Army, Air Forces, and Navy), and to other readers,
interested In the theory of jet engines.
COVERAGE: This volume constitutes the first part of a 2-part vork on the theory of
aircraft engines. Part I presents the fundamentals of thermodynamics and gas
dynamics; Part II will discuss the theory of jet engines. Chapters 1, 111, and
IV were written by E.V. Rovinskiy; Chapters II,, V, VI, VII, and VIII by Ya. Yx.
Madorskiy. A section on possible atomic aircraft engines is included in the
Card-l,(6

Theory of Aircraft Engines (Cont.) SOV/4229
general discussion of aircraft engines. The authors thank Docent Yu.M. Mayzell,,,
Candidate of Technical Sciences. The work of G.I. Petrov and Ye. P. Ukhov
is referred to in the discussion of shock waves and diffuser design. There are
13 Soviet references.
TABIE OF CONTB7M:
Preface 3
Ch. 1. General Information on Aircraft Engines 5
1. Concept of thermal engines 5
2. Types of aircraft engines 6.
3- Classification of jet engines 8
4. Thrust. Specific jet-engine paraneters 11
5. Gunpowder rocket engines (PRD) 15
6. Liquid-fuel rocket engines (ZhRD) 18
7 Renjet en nes (FM) 23
8: TdrboJet gnigines (TRD) 25
9. Turboprop engines (TVD) 27
10. Atomic ai7rcraft engines 29.
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ACCESSION NR: AR1402235 S/O124/64/ooo/oo6/vo77/vo78
SOURCE:. Ref. zh. Hekhanika, Abe 6V640
AUTHOR: Rovinakiy, B. M.; Lyutteau,. V. G.
TITLE: Certain results of study of stress relaxation in metals and alloys
CITED SOURCE: Sb. Relaksate. yavleniya v met. i splavakh. M., Metallurgizdat,
1963, 275-289
TOPIC TAGS: stress relaxation, metal, alloy, relaxntion curve$ reverse x ray
method, deformation, elastic deformation
TRANSLATION: Describes new methods of obtaining relaxation curves by measurements.,
of t'
"anaver8e deformation of a test piece whose initial longitudinal deformation
remains constant, and a reverse x-ray method of transverse elastic-deformation of
lattice (at room and elevated temperatures). The latter is an adequate method
of load meacurement, necessary for maintaining given initial deformation with
strict constant longitudinal deformation of test pieces Analyzes the relaxation
112

ACCESSION UR: AR4042235
curve equation and considers structural changes in metal during stress relaxation.,
The x-ray method shows that,in the process of stress relaxation,structure per-
fection of reflecting cryatallites decreases and coherent constraint in them is
disturbed. Simultaneously there occurs a turn of grains and their mutual displace-
ment. Thus, basic mechanism of stress relaxation in metal (at room temperature)
is cla8to-plastic, a shear mechanism. Stress relaxation is noticeably influenced
by magnitude of grain, degree of preliminary plastic flow, content of impurities,
test temperature, distortion of lattice,and level of constraining forces. Hardness
of HB metal, similar to relaxation stability, is determined, on the one hands
by substructure and, on the other, by constraining forces.and distortions of lat-
tice. Therefore, among these mechanical characteristics a correlation is observed,,-
Bibliography! 13 references
SUB CODE, MM, AS ENCL, 00
.212-
Card

-es in ~~.aD-Jte matter'lals to -wear.
~N SSSR 160 no.4:EO7-810 F 165. 18:2)
1. Gosudarst-vermyj nauchno-issledova -lei institut mash-ino-
vedeniya. Submitted SepLember d", 1964.

L 43884-65 EPF(c)/EFR/LztlG(j
~/JD/
W/W VDJ
-,-'AP50 853'.- -
06
ION. IM

10
L-011290-67 Wr(m)/TZm(t)/TrT Tjp(c) ip
AP6018949 SOURCE COM: 'UR/0126/66/021/006/0929/0934
AUTHORSs Rovinsk1jy#..B*_M*; Sinayakiyp V. 14.; Gallperin,, H.Jas
ORG; KII for Machine Design (NII mashinovedeniya)
TITLE: Inv efects ariging in metals due to metal
patigation of the stability of d
fatigue
SOURCE: Fizika metallov i metallovedeniye, v. 21, no. 6,. 1966t 929-934
TOPIC TAGS: aluminum metallurgy, copper, x ray diffraction study., x ray scattering,,
metal crystal
ABSTRACT: /he stability of fatigue defects in metals was studied on both aluminua
and-goppef'specimens.. The study supplements the results of an earlier investigation
by B. M. Rovinskiy and.V. G. Lyutsau. (F)24, 1961t 12, 305). The work waft carried
out by measuring the change in x-ray scattering4w the metal specimens in the fa-
tigued and relaxed state. The affect of ~gingfon the plasticity and durability of
cyclically deformed copper was also studied The experimental data obtained in
this part of the investigation were treated after the method of N. W. Davidenkov
and G. T. Nazarenko (ZhTF., 1953, 23.9 741). The experimental results are presented
graphically (see Fig. 1). It was found that the intensity7 of,scattered x-rays,is
notably deplandent on deformation of the cry tal lattice (caused by the cyclical
deformations) and on aging (connected vith the relaxation of the deformed crystal
!Card 1/2 UDCi 539,43:539-292

L 042go-67-
ACC NR:
AP6018949 75 AW
2S w
0
I
Fig. 1. Integral intensity of the Debye stani AOj
line (400) of cyclically deformed.copper Q, -
as a function of aging period. Solid 120
dots represent the relative scattered 2
intensity for the specimens in the initial

state. 1 - 107 cycles C- 10 1
Cgi
-

max .10
150 0 M
6
2 - 10 cycles 0- 16 kg/Ma2; aging
Time ho)irs
1 7
max
temperature - 80C.
lattice). The authors conclude that the vacancy and micropore defects heal with
time, provided that the latter are smaller than ~, (critical)p that vacancies are
precipitated on pores and cracks in excess of A (critical)' and that a general
coagulation of micropores sTmIler than ;~ (critical) takes place in the aged
specimens. Orig. art. has: .4 graphs*
SUB C~OEE: ll/ SUBM DATE: 02JU3.65/ ORIG REF: 0051 OTH PXFs 002

2/2
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