SCIENTIFIC ABSTRACT PAVLOV, V. A. - PAVLOV, V. A.

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• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001239620014-3
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: January 3, 2017
• Document Release Date: August 1, 2000
• Sequence Number: 14
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

SOV/58-59-5-10700
Translation from: Referativnyy Zhurnal Fizika, 1959, Nr 5, p 118 (USSR)
AUTHOR: Pavlov. V.A.
TITLE: Study, of Regularities In Plastic Deformation and Pallure
PERIODICAL: Tr. In-ta-fiz. metallov..Ur&l'skiy fil.-AS-USSR, 1958, Nr 20, pp 245-263
ABSTRACT: Survey of studies executed in the laboratory of mechanical properties
of the IFM, The bibliograpkiy contains 57 titles.
Card 1/1

S,`V/126-6-1-111/33
'AUTHORS: Grin') A. V., Pavlov, V. A. and Pereturina, I. A.
I ____
TITLE: In f 111 c n c e o f 87t a t i c D-1 Ws 76-FT6 ns o f t h o Ci-f s lu;_~ I Lat, t i c e
on the Nlechanical Properties of Aluminiwa-Mz.t~,nesiuiu
Alloys (Vl-ivaniye staticheskikh iskazheniy
reshetki na mekhanicheskiye svoystva splavov
s ina6niyem)
II Dependence of the Total and of the Uniforia
on the Temperature and the Speed of Defor;,,i.,ition
(II Zavisimost' polnoy i ravnomernoy deformatp-1-i ot
teimperatury i skorost-i deformirovaniya)
PERIODICAL: FJ.ziha Metallov i rile tallovedeniye., 1958 Vc! b
pp 110-115- (USSR)
ABSTRACT: The aim of the work desc-,-ibed in the first Part of' LhiS
paper (19')?, Vol 5, fir 3. pp 493-500) was to study thin
influence on t-he Fv.e3hanical properties of trie static
distortions of the CrySta.1 lattice which are c_iusec,
atoms of the dissolved elements and the diffusior.
processes taking place as a result of stresses occurr
during plastic defori~,Lation., Aluminium-magnesium alloy,'3
were used in the experiments, Earlier invf.-7F~ij:, uf
Card 1/6 one of the 1-tuthors and his team have show.n that

SOV/126-6-1 -I 4P
Influence of Static Disto-tions of the Crystal Latt_~ce on th,?
Mechanical Properties of Aluminium-Ida.6nesium Alloys
II. Dependence of the Total and of -the Uniform Deformation on the
Temperature and the Speed of Deformation
considerable static distortions of the cryst'-1 2a-ic-e
take place.which are brought about by ma6nesiu_,:- ato~-_E-
but the bond forces do not change the composition Df ti-t
alloy. Such a combination of properties permits
studying in the pure form the influence of crystal
lattice distortions on the mechanical propertier-, T171.e
authors investigated the temperature dependence of 6'7~e
yield point and the ultimate strength of pure alumin-DL:
(contqining about 0.01% LIG. 0,0017% Fe, 0.0014% Si,
0,0011% Cu) and its maGnesium, alloys (0,05, O~15 0,3,
O~5 and 1% 11g) in the temperature range between 80 and
7000K for widely differing defonnation speeds ((;,4,10-3
2zlO- 1) 2-10-4 )_ It wa-~ established that for Pur,,,
aluminiu.,zi the temperature dependen 8e of the yield pci:~-,
in the temperature range UP to 500 K is determined
fundasnentally by a chan6e in the interatomic bond forces,
At elevated temperatures a more pronounced dependence
Card 2/6 wao detected of the yield point on the temperature which

S~-'V/126-6-1-14/ 73
Influence of Static Distortions of the Crystal Lat-ice on -~.te
Mechanical ProT)erties of Alumini,,r.,i--11aE:neFjium Alloys
H. Dependence of the Total and of the Unifonn Deformation or. the
Temperature and the Speed of Deformation
is apparently due to deformations along the grair
b o una ar ii~ -q .Hardenini., cf the aluminium alloys v.-it'l-
magnesium is caused by static distortions of -L..e
lattice v:hich are brouL;ht bbout by magnesium atom.,.. Tfllc,
diffusion processes, lead to a non-monotonous
of the yield poin4- on the te.;~perature an
dependence on the Fpeed of delarmi-,tioE and a
of the deDendence of the mechanical prorprtieF on
c~~i~lposition of t'--.e al-lo,i and on the condiLior.E of
defo-nj-iation, observed of the, yield
-!Ti the te:-,perat'--tre ran,,-e of about 1;0
0 00 K and increased
values at 80 K which are atti,ibuted to various Lj~i-, Cf
diffu--ior. processes takinC, place in the case of
deformation under the effect of stresses T h u si r
found that static distortions of the crys'"al lattice
brought about by the magnesium atoms,,cause an increase
in the yield point and the ulti-mate strenEth, In the
Card 3/6 here publishea second part of the paper, the au'hers

SOV/ 126-()'-- 1 - 14/33
Influence of Static Distortions of the Crystal Lattice on ~;'--.e
Mechanical Properties of Aluminium-Magnesium Alloys
II, Dependence of the Total and of the Uniform Deformation on the
Temperature and the Speed of Deformation
investigate the total and the uniform deformution of
alloys of alumini~u6 1.,;ith magnesium in the temperature
range of 80 to 700 K for the same range of speeds of
deformation, They found that the static distortions
of the crystal lattice caused by magnesium -toms
reduce the plasticity and that the diffusion processes
taking place a's a reculr, of' the r3trenflen durJng
deformation of alloys bring about an increase In Wie
plasticity and complicate the temperature dependence of'
the total and the uniforin elongations, In alloys of
aluminium with maGnesium, the crystal structure of which
has suffered static distortions, a complicated der----ndence
is observed of the total and the uniform elongarioris on
the temDerature and the speed of deformations, Tne
plastic properties of such alloys is apparently
determined by several factors which act simulta-ne:~usly,
namely.- a more unifGrm distribution of the plastic
Card 4/ro deformation alont: the volume of the crystal and an

SOV/126-6-1-14/3z
Influence of Static Distortions of the Crystal Lattice on t--e
Mechanical Properties of Aluminium-Magnesium Alloys
II, Dependence of the Total and of the Uniform Deformaion Dn thc-
Temperature and the Speed of Defor-.,,iation
ii~-crease of the effective vc1u::ie which r)arti--irates,
the defor.:ration, brint;s about an increase i,.
plasticity of the alloyF; ~~ diffusion of tne itomS of
alloying elewents under the effect of stre3--s talzi.-.~,-
place during defor-,Tu~tion and caucine, a re~-I-tion of
PeCLRE of Ovel--,~trcsf-vs in t-1- neiF,1hbc,,i!-hu-,-! cf
unifori.rii-,ieo of the cr-vsLal lattice and ir tno
hcod or microscipic cr-acks brintf. aho--)t aL increase (:.f
plastic -.,.Y-; P- increage of "he types II ana III -ij sc,
duri-Tig plastic ar increase of the
resistance t(, def.)r::i~atior, i:i the alloys brin.: about
-educt4-ori 'Lr, th,- 711c-tS+~iCit--,
the
of these factors Will c~3use a suff-'cienti-, --oziplic-ated
dependence of the un-iform and the total eloni~ations on
Card 5/6

S0V/l2G-6--j_jLt,/53
*Influence of Static Distortions of the Crystal Lattice Dn t1le
Mechanical ProT)erties of Aluminiuz-i-Magnesium. Alloys
II. Dependence of the Total and of the Uniform Deformation on the
Temperature and the Speed of Deformation
the composition of the alloy and the conditions of
deformation.
There are 7 figures and 9 references, all of whic'n
are Soviet,
ASSOCIATION: Institut fiziki inetallov Urallskogo filiala All 3SSR
(Institute of Metal Physics, Ural Branch of the
Ac.Sc., USSR)
SUBMITTED: August 11, 1956
A I mnln wn -magnes .4unt a _!1oy,,;--1,1e,2h an i L- a i prcpp r t i
-rYL3ta 1c;-Def'ormation 3 . C'ry s t a Ls - - 1,471 t , i ,, r-.,
~~ard (16 4. :~ry~stal~;--Metailurgicai effects

AUTHOR: -P-av -L -1 -- SO -Ir- /7 7
TITL---' Internal Lattice Defec-.s S-Iudie-~J Irze--. F~-
(Izucheiii~-e defektc)v kristallicheskoy reshell- !,I
pomoshchi vnutrenne6o ti-eniya)
PERIODICAL: Fiziku filetal.lov i Motttllovedeniye . 1958 V I I
,,) r I-j
, 12~1-1 7 (USBR)
ABSTRACT: Pure Al azid A! + 13% IME~ were used at or belt-
tem7,erature; 0peay-s are foLuid in -50 t- --,O-C
-170 to -160 C rankled-, plus a rise at
~(,tivAioti onor~;ies rire 0,~ u~jlf
0,0'- eV, Trr,ns vers-- oscillations a t 1-100- 1 "010
used , i:i sin not described (whet!.,-,.
rct is r~c'~ st&t"Q)~ Roand rods 200 aai Ion.: I-Id 1 iui~
diamete--' (p-r~~Ta.~ation rot desc--ibed) ,~.,ere ~-.Ee~~ F-I'-F
and "I
- show ti,ec-e ti,o peaks, for pure Al (1)
arid 4 shm; rather
Al al'oy (2). F i gq ~
ieasure2ents in the immediate regions of
Doubt 1*6 c,-Ist on the
since tne peal-I height very muo.~'i oi.
history~ Pi-eferenc-u is i;iver, to Frenkel s int.-7-,
Card 112 atoms thuoi~,7, (Ref.IC'-'., par~liccularly ii. I-

SOV/126-6-1-16/3;
Internal Latticu DOI-Octc. 13tudiud froin Intornal FrIctior)
rise at very low temperatures. The other tvio peaks
(in order of increasing temperature) may be explainal,le
in terms of diffusion of vacancy accumulations, and of
clngln vacanclori respectively. Figs, 5 and E show ~Iie
effects of amiealintL at 150,C for *~, houi-.- ,it,
times after annealing; the first peak becomes lower and
the second higher, This is interpreted as the
vacancies combining,
There are 6 figures and 18 references, 4 of which ar~~
Soviet, 14 English.
ASSOCTATIO14: Institut Fiziki Metallov Ural,skogo Filiala Al; SSSR
(Institute of Metal Physics, Ural Bra-nch of the Ac Sc USSR)
SUMUTTED: July 26, 1956
1. A-' -zLinum-- Lattices Alumir,-=--Temperatari~ -fa-tc-E
Card 212 3. alloys- Lattices 4 A-' rr-,'!
Lnagnes'--m alloys-Temperature factors

AUTHORS: Noskova, N. 1. ard Pavlov, V. A. SOV/126-6-2-21/7a
TITLE: Investigation of tH~;-YEff6--STfU-ture of Solid SolutiDLs of
Aluminium with Ma~Lnesiun and of Nickel with Copper
(Issledovaniye tonkoy struktury tverdykh rastvor,.~v
alyuminiya s maSniyem i nikelya s med'yu)
PERIODICAL: Fizil-a Metallov i Metallovedeniye, 1958, Vol 6, Fr -1,
PP 334-138 (USSR)
ABSTRACT: The t.ork, described in this paper consists of' ate:j,~u-irit~
the static and dyflamic distortions of the crystal lattice,
determination of the block pattern in the defor:aed state,
ii,easurement of type II distortions and deterfillination Uf
the temperature dependence of the "static" dist(-rtic)r-,s
for the solid solution nickel-copper. The followin,.- .ere
investigated: 1) pure aluminium containing 0.001?% Fe
0.0011% si~ 0.01% magnesium; alloys of aluminium with
0.12 and 0,04% magnesium.
2) Pure nickel obtained by fusion in a vacuum furnace aLd
alloys containing 10, 20, 40 and 600/6' copper also produced
in a vacuw.,i furnace.
The Speciffiens for investigating the static and the dynaiaic
distortioLs were produced as follows: powder pro(iuced by
Card 1/4filing and passed through a sieve was annealed itri vacuum,

SOV/126-6-2-21/3L~
Investization of the Fine Structure of Solid Solutions of A'L,,I:,,,iniU.L
with Ma6nesium aria of 14iclkel wituh C"opper
whereby the annealinF, regimes were so chosen (Table 1 ~,55)
that the eyt,inction effect is eliminated. The annealed
powde;, iva,- onto a copper wire of 0.3 min dia; the
specImen diometer was 1.00 + C.02 mm, The chnr~ict.eri!..tic
temperat.ure of the pure met9ls and of the solid -,c)1-d*.,1.0riS
dete_--::.,ined by decyphering X-ray patterns obta~,.Pd Zro.-.
the investi6ateLl ,.peci~ens at the temperatures of
ni-troben, +120 nnd -1100 C. For determilninE; the tjpe II
distortions a-ad the block pattern, the fili%s vie-e nor
anrea.L-d; the f-lin6 and the exposures for nicke'_-ba--e
alloys were offected nt. room temperature, Powder.- of
aluminium aiid of alloys of Al with waGnpsi7Lin wore
produced by filinE at liquid nitrogen temperature, si-ice
for the filine, carried out at room temperature thl~ t-.11pe IT
distortions become eliminated and the X-ray Patterns dc :-ir
reveal any blurred lines v-.-ith a high degree of reflectioi..
The type II distortions in aluminium. and aluminium alloys
viere determined by using copper K -radiation; all the
other imeasurements were effected 11bith a molybdenum K
Card 2/4radiation, In the case of nickel specimens, aluminitL ~'.nd
SOV/126-6-2-21/74
Investigation of the Fine Structure of Solid Solutions of
rith Magnesium and of Nickel with Copper
zirconium filters (d = 0.22 mm) were used. Calculation
was based on the lines with differing index squaras
(20 for aluminium and its alloys, 24 for determining type 11
distortions of nickel and its allcys, 68 for acter.aininb
the characteristic temperature). All the lines
photometered at least three times. Thereby, the accuracy
of the characteristic temperature was 3% of the mebEured
value. On the basis of the results, which are grn-hed
and tabulated, the following conclusions are arrived -..t:
1. In the investiLated solid solution the ty-pe Il
distortions increase with increasing content of 'Lade sucond
component ir- the solid solution, whilst the degree of
block formation in the deformed state (90% deforu-,,,,,tioi,)
chanEes lit-,le as a function of alloying.
2. A possible cause of hardening of the solid solutio-ns
of aluminium with mu6nesium is the presence of lt!r e
static distortions caused by the atoms of the second
component,
3. Iri the solid solutions nickel-copper hardenint, is
Card 3/4
observed in spite of the presence of the dynamic

SOV/12C-E -2-;? 1/ TL~
Investigation of tie Fine Structure Of Solid Soluticnc ol -,I
with Magnesium. and of INickel win Copper
distortions ~the characteristic temperature aF
of decreases). The latter can be e3ucid,-te',"
the formatioi) ',-n t~.~c solid solutions of ;alcrc~f,cop 1, -
unifuriiiitles -v.hich iTilpede the processed--. of i)lii~~Ilic
deforwation Lmd of relaxation.
There are ~ figures, 3 tables and 7 referenceF:, 5 of
%-.hicl-, are Soviet, 2 German.
AS.'I_-:0CI_ATI0I,'-: Inst~Lut fiziki metallov UFAII SSSR
(I.,istiWte of i,lietal Ph7sics, Ural Branch of the A-,Sc,
USSR)
SUMIITTED; July 119, 1957
laard 4/4 1. A'L"Mdnum ailoys--Structural analysis 2. Nickel alloys--
Structural analysis 3. Alloys--Production 4. Vacuum furnaces-
Appill-cations

AUTBOM3: GoyduJ-.(,v, J. G. ~,~: I"
TITLE: stresE i7_717,77-7-i -ic-'el Cn"_ r
( R e 1 ii 1: P3;! L.,; iy LI n, ~ p i,- v 1 .1 P v --; ~"'r r, "?, ~ , ~! e " ' .-IT 11 1,
PERIODICAL: Fizil,,i V(~l
Pp 517-521 (US"171,')
ABSTRACT: In earliei (Refs !i;ill 7) investiLAiun.,-,
describej cf -'e
intte:r,,toinic bon(d fcr,~cs 1.id not depoild ori L! '_~ c~ ILC 'Fiul
of tite soli, -' E-,)1utiur, Pnd the ,Aatic U F'.
crvst~'l 1;~ttice d~-,cren-icu iiicrea-~ir
In~reas,e_, t),e iielr" the ulti..~.ate Et_en~ c'r,
thc rolLx~,tiun ~-,tat ilitj .;e:-(-_, observed in -_C~
(Refs 1 and Further.:.ore, diffusic,it c:
:ii,qgrjeEiLL_. redisul U"lUcin i"si"10' thu vuloj"~.!
S,) JU- 4
,_C111 v;t2re ob.,_-ervecl undc.r. 1c)~:,d,%,hicl
nozj-:"1O1_u tollo k's cl-'allz'e Uf t)!C
f urc t i c). ~ u f u'-, e t e..ipe r,~.. ture anCl t he e f rn-, t i C" F e
Such ., if f usi,, n : roc e P., e E, brour_~ t aboL~ t Fic f,
di_-tr~batloii of tl-,e t:.EIGne,.liu_i alcjn~ e
Solid s3lut'L_11; t"is E!ccc~~,il_)Bnied b.-i
Card 1/6 act. :f dif tusion ~~._d 11:cl'~-:

Stress Relw-,,i(;-IL(,n in uf Lickel -. i~!' COp1wr
recj jstalli.-~~ tion Le..ipenit-Ure ~,ihich in turn
develop a-, e ,. t L) f J i f f -, i.,, i (. i ~ 1) 1 --. s t i c i t y . 1: 1 rAccel-co[per
is an in~~ve dmp in t, i e a krac te-r- is tic tanpEmbx~e and the . I ~j a : 1
elasticity decreases -.-nd 5). The stL ---Ic'
distortionf,7 of t! e lattice tire ccnsiden.t` Ile Lit
room te:,.Teraturc but f,hey docreLlse rnpidly
te:-per-,~ T=e , D. cop-,,er-rici deformed ,Illoyr in
o.-L' the inte,--atcmic Lond forces %,as obsc,-rvt:-d is
. d~j
probabl-, -e to the iion-,iniforn distributic,.,- of
Jn the volu!nc of the ,w)',id ~~(jlutlon,caused 1',,
durinE defci-m.~ ~,Iui. ru.Ld 1101dint.-, c-f tI,,e :;.t r ou-
te,averEture after in these :Illo,.,-
form&tion ~ari-L of the K-st-ite il-
,os!
J.L
ato:as of cc:p3lr~~r --olid ,clution (Ref,
into consldei-~,L-1,3n pr-perLies, of ~A,e nicl:el-ccpp~Ur
alloys, iL be th-,~t inte-:.~~iv(j
urocess,,-F, p1race uiid(~,, , '-,ich an-
intensin s L r(~!, -e ' -c o n. 17 u.% e ve r, ~i i f fi I,,- ri
Card 2/6 stres,~~ ill lrin,~
L~

V112(- -;,-a
Rf

in
-0
1
f

f
u

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.
T

f

C7 i
f
t t; f
re ,
c n it i
Card 5J0 55Q C
)o
3/6

~3~ V1126--

Stress -qel,.-- n

j'.

t r C. F; f
t
e S
50
iL

f F" o 5
jvt'll
)r
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curve ra Fi
71:
-1 p e
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iF.
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Card 4/6tll e

,~',V/l 2~,-(-- 21- 1917~2
Stress Rela.-ation in Al 1,:, Ivs of 1; Ic ke I v i Co: ,,er
to slidin,' or if the stre-.E
relaxatio:i is predc):;.ij,'i.--1,' -ae ~u the slidiii,
those alloWs are L~Jle v.L.ich have tl-_C, h-j- r,e-
j , t
copper content; in tLc c:--ie thLtt the difusion
I
is predo-ainant, stress rela---1;,tion will be the ...-ire
pronounced fhe ` thu concentration of
in the ,ase of --, ~ffu~~iun under load, non-unif~ir.-.-
distribuuiwi of Lhi-~ ir~ the volLLnc of t'l,e
solution v.,ill take jA'-ce,-.,,i.!L;h is uccomp~-,iiled by
hardeninu -f the cG-,)per-rich alloys (40 to 1605~ Cu) durin-
the process of relaxat.ion, In an appendix,thQ , .-rk of
Kester :.nJ Schulle, Zs.
quoted; the~~,2 fOLI.11(' that there %,.as iL
the prupertitjs uf the nicl~el -:jlloy coi1tLini!;'
after ztanealin,,, in the te..iperz.Ituru ran.~e belov, 65'
is attributed t, Lhe occurr,~nce of near-orderi-,,., in this
teriipor:it~u,e ron_e. It i-,~ st~ited thbt tfieic;e dual!
the asow:,ptiui, of U1-: :tuChurs of Lhif; ptiper (-if t~ie
pos~ibilit,Z of of the (Im-ill,
Card 5/6

Stress Relaxation in Allo,',.,~' of iiicl--c-1 with Col)per
rela)~ati,.~n as a result of near-orderin6.
There L-re 2 fi6ures, 1 thle :.,iid 10 referen(.e_-, of
which are Soviet, 1
ASSOCIATIOE: Inst~:_ut fi~~ihi _-:'iet-L~11ov Ui-allskoo
(Ins-uiLute. of PhyEics, Ui,,,--,l Braiich of L!,e Ac.S,2.,
USSR)
SUBMITTED: July 26, 1(57
1, Copper-nickel ailoys--Physical properties 2. Copper-nickel alloys
-Diffusion 3 Copper-nickel ailoys--Stresses 4. Copper-nickel
alloys--Temperature factors
Card 6/6

~30V /12-6-~,-4-21 / 34
AUTHORS: Pavlov
Pereturina. I.A.
TITLE: Mechanical Properties of the Nickel-Copper Alloys
(Mekhanicheskiye svoystva splavov nikelya s medlyu)
PERIODICAL:Fizika Metallov i Metallovedeniye, 1958, Vol 69
Nr 4, pp 717-?24 (USSR)
ABSTRACT: The effect of the temperature and the rate of
deformation on the yield point,47, of pure nickel and
its alloys containing 10. 20 40 and 60% copper was
investigated. High purity electrolytic nickel
and electrolytic copper with less than 0.05% Jj4purities,
both degassed by re-melting in a vacuum of 10-5^mm Hg,
were used for the preparation of the experime-n-tal alloys
melted in vacuum. The ingots were forged into 10 x 10 mia
rods whose size was then reduced to 5--x 5 mm by rolling.
This was followed by several wire--drawiig operations with
.L.",..a~~mediate anneals. The conditions of the final heat
treatment were adjusted so as to obtain the same grain
size (approx 0.1 mm) in all tLe investigated alloys.
The tensile tests were carried out on wire test pieces
Card 1/6 (1 mm diameter, 55 am long) at temperatures rangi-ng

1, ov / i ~-' 6--1,
Mechanical Properties of the Nickel-~;opper Alloys
from -1~6 to + 7000C and at thrae rates of strain:
2 x 10-1p 6.4 x 1o-3 and 2 x 10-1 cm/sec, The graphs
showing the temperature dependence of (F of pure nickel
and its alloys deformed at various rates of strain are
reproduced in Fig-1, 2 and 3. The variation of Cj of
pure nielml with temperature is very small up to t)uOOK,
while above this temperature it decreases ejonentiall7.
(The C -n G versus I/T graph is shown in Fi go It is
easy to show that the temperature dependence of G in the
low temperature region i6 aetermixed mainly by the
variation of the atomic boad forces with the temperature:
Graph I in Fig.5 shows the Lemperature dependence of the
yield point/elastic modulus ratio (O/E) for
poll crystalline a4cxel. It can be seen that up to
60% this ratio remains practically constant. (In the
case of a single nickel crystal, the temperature interval
within which 6 varies little with temperature is even
wider, as is shown oy graph 2 ir- Fig.5 which represents
the temperature dependence of r/E, where c is the critical
Card 2/6 shear stress). This effect which has been also observed

Mechanical Properties of the Nickel-,opper Ailoys
in aluminium (Ref-2, 11), copper (Ref.12) and gold (Ref.10)
appears to be a characteristic of metals with the face-
centred cubic crystal lattice- The yield point of the
Ni-Cu alloys is higher than that of pure nickel and
reaches its maximum value at 40% Cu (Fig.2). The fact
that G of all alloys is greatly affected by temperature
cannot be explained by the variation of the atomic bond
forces with temperature: The temperature dependence of
G/E of three alloys deformed at the same rate of strain
is shown in Fig-6, and it is quite apparent that this
ratio depends to a considerable degree on the temperature
at which the alloy is being deformed. 1n addition, the
variation of G with the temperature is not monotonic:
The O/T graphs show two maxima, one in the high
temperature range, the other approx 2000K. The
magaitude and location of theso maxima depend on the
composition of the alloy and on the rate of strain.
In general, the magaitude of the critical point (U.T.S.)
increases with increasing copper content up to 40%o Cu
and then decreases. However.. more careful examination
Card 3/6 of the strai-a/stress curves reveals that the increase

SOV/126-6-4-Pl
Mechanical Properties of the Nickel-Copper Alloys
of U.T.S. is associated mainly with the increase of'
the yield point: If the strain/stress curves of the
investigated alloys are drawn together in such a way
that the yield point coincides with the origin of the
co-ordinates; it is seen tnat the increase of the stress
due to strain hardening is less in the nickel alloys than
in pure nickel (Fig.?). The experimental results are
correlated with those obtained by other workers and the
following ronclusicns are reached-
-he aLimic bond forces and static
(i) The variation of t
lattice distortions cannot account for the increased
strength of the Ni-Gu alloys, sInce the former decrease
with the risi-ag (-u content. while the lattice
distortions at temperatures higher than 3000C are quite
small.
(ii) The increased strength of 'the investigated alloys is
caused mainly by non-uniform distribution of the atoms of
the alloying element in the solid solution, It is
postulated on the basis of the experimental results that
Card 4/6 there are three possible causes of non-uniform

6 OV/12t--6 -4-211/--:
Mechanical Properties of the Nickel-Gopper Alloys
distribution of the solute atoms; (a) High concentration
of the atoms of the alloying element at the grain and
sub-grain boundaries, (b) Formation of solute atom
"clouds" around the dislocations, (c) Short-range order
i.e. deviation from the statistical di.,:tribution of the
solute atoms in the solid solution,
(iii) The yield point of pure nickel cons:Lsts of two
components: One due to shear within the grains whose
value changes very slightly with the temperature and
the other due to shear along the grain boundaries, the
temperature dependence of which is approximately
exponential.
(iv) From the non-monotonic character of the temperature
dependence of G , and from the effect of the rate of
strain on this relationship, the diffusion character of
Card 5/6

S0V112&-6---L---1 -14
Mechanical Properties of the Nickel-Gopper Alloys
the interaction between dislocations and the solute
atoms (or groups of atoms) can be inferred.
There are 9 figures and 30 references of which 18 are
Soviet, 10 English and 2 German.
ASSOCIATION: Institut Fizik-i Metallov Urallskogo Filiala Ali SSSR
(Institute of Metal Physics~ UrAl Brarwh of the AS USSRj
SUBMITTED: 5th August 1958,
Card 6/6

AUTHORS: Datsko, 0. I.Iand,Pavlov, V. A. SOV/126-6-5-21/43
TITLE: Temperature Dependence of the Internal Friction in
Pare Nickel (Temperaturnaya zavisimost' vnutrenneSo
treniya chistogo nikelya)
PERIODICAL: Fizika Metallov i Metallovedeniye, 1958, Vol 6, Nr 5,
pp, c)00-904 (USSR)
ABSTRACT: The authors used electrolytic nickel of 99.98'?0% purit:r.
Ingots of nickel were rolled and drawn at room temperature
in several stages until a wire of 0.80 mm dia. was
produced. In b8tween the forming stages the samples were
annealed at 800 C in vacuo. After the last Rnneal the
wire was deformed by 80% reduction of its cross section
and cut into 300 cm lengths. The temperature dependence
of the internal friction was determined by means of a 4
1 .5 c/s in 10- - 1
torsional pendulum oscillating at 0 3 0-
mm Hg vacuum. The following procedure was applied 0in
each set os measurements: a sample was heated at 2 C/mir.
to 700-900 C and then cooled slowly to room temperature
by switching off the furnace and leaving the sample in it.
After each such anneal the temperature dependence of the
Cardl/4 internal friction was measured and recorded. In the first

SOV/126-6-5-21/43
Temperature Dependence of the Internal Friction in Pure Nickel
heating of a deformed sample to ?~O`c or more,
recrysta-li.isation occurred at 4~)O C. Each subsequent
heating produced collective recrystallisatior. F4g.1
shows the temperature dependence of the internal friction
of nickel as a function of the ar-real temperature.
Curves 1-5 in Fig.1 represent IV-lie results o8tained by
short anneals at 700, 750, 800, 850 arA 900 0 respect ~11(-"!Y'
while curve 6 is the result of a 5--hour anneal at 900 C.
Fig.2 gives the temperature de-)endence of the internal
friction of nickel as a func-lior of deforinati8n by 1%
(cuEve 1) and subseqgent short a-aneals at '(00 C (,~ur-,-,e 2),
8000C (curve 3), 900 C (curve- LL), and a ~-hour arLneal at
900 C (curve 5). Fig.3 pres,ints :Bata, analogous tc t~-~,~se
of Fig.2 for 20~ deformati,:~n (curve 2) and subsequ-~nt
anneals at 900 C (short anneal, curve 3 and 3-hour, curve 1).
FiS.4 shows the effect of addition of 0.023% (curve 1),
0.05% (curve 2) and 0.24% (curve 3) of aluminium on the
temperature dependence of the internal friction of nicke--'-.
The authors make the following conclusio RS.
Card2/4 1. The internal friction peak at 440-460 C is due to

SOV/126-6-5-21/43
Temperature Dependence of the Internal Friction in Pure Nickel
relaxation stresses along grain boundaries. This peak
decreases in amplitude and is slightly displaced towards
higher temperatures on increase of the annealing
temperature. This is due to the increase of the grain
size and the change in properties of the grain boundaries
on collective recrystallisation. 0
2. Tho intornal friction peak at 630-800 0 is due to
relaxation of stresses on mosaic block boundaries. It
increases in amplitude and is displaced towards lower
temperatures by plastic deformation. Increase of the
temperature of anneals carried out after deformation
displaces this peak towards higher temperatures and
reduces its amplitude. This behaviour is due to processes
of growth and reduction in size of the mosaic blocks,
which are accompanied by changes i-R the properties of
the block boundaries. The 630-800 C peak disappears
when a foreign metal (e.g. aluminium) is added to
nickel (Fig.4).
There are 5 figures and 14 references, 4 of which are
Card3/4 sovietl~ 6 English, 2 German, 1 French and 1 translation
from English.

SOV/126-6-5-21/43
Temperature Dependence of the Internal Friction in Pure Rickel
ASSOCIAMON: Institut fiziki metallov Ural'sko6o filiala AN SKR
(Institute of Metal Physics, Ural Branch of the Ac.S,-.,..
USSR)
SUBMITTED: kugust L', 1957
Card 4/4

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NDCM I EVM

SOV1180- 59-1-21/29
AUTHORS: Izbranov, P,D., Pai,-r,-,,- V A'and Rodigin, N.M.(Sverdlovsk)
";a
TITLE: f r, a Orisn "tion of Recrystallization
Investigation
Centres at High Rates of Heating (Issledovaniye
orJ,~entatsii tsentio-,- :-ek-:-Istallizatsii pri bollshikh
skorostyakh nagreva)
PERIODICAL: Izvestiya Akad-4mi-' nauk SSSR, Otdeleniye teklinicheskikh
nauk. Metallui-giya i toplivc, 39"-",9,Nr 1,pp 109-110
+ 1 plate (USSR)
ABSTRACT: The authors suggest -,,,a-. mo-Te :reliable res-Its on
recrystallization (-.an be obtained through investigation of
the or-4entatior. )f %artr9s, at ILigh !~~.aat,lng -,a"-,Ps than at
the low _^ates ,t_-,ed in mcst h-.,)rk. Tll--.ey go cri tx_ describe
their of th e r stall i zation of -;old-
rolled spe~.J.mens cf a 3.',-~% Si steel, One bat--h of test
pieces was '5% :~-ed-aced, t-lie -tl-ier by 95%. The 15xlOOxO.25
-td altaer by the passage of
mm strip s~e,--m-ins were 1) ea e J_
electricity, ir. Rr~digin-s apTaratus (Ref 10, or by
immeroic~n ir a hc-.. salt bath and air The cold-
r-'eformed and xa-~.ristall-42.ed spe,.~~m6n3 were examinr:ld
m1,jrosr,,opi(.aliy -ind their teXt'.1L!'a was determined by the
X.-ray zneth:)d, F-g, 1 shows tlie X.-ray pattern obtained
Card 1/3
from a spe~~iman, Fig C'--' tl7iat fr_)m, one

SIV/1-_~,D - 159-1-21/29
Investigaticm -~;f r,!,;3 -.,f Recrystailizatior, Gentres at
High Rates of Heat`~.-.z
rer;rystalLiz~?d "- '-aat-_.-ig ar, I1000C per sec.
to 7',/:~,~-C, Fj,,- -,, '-,a,~ ~,r_e -immersed for abo---t- two
sa--,:nJs : .Ln a sal' ath at F-g 4 sh,),ws I; .n9
st-~,uctu-_,Es with rh-s latte:, p:,-.)ced-a.,-I. TLe X-ray
patternc, c-A.a .1ong e--- iiea'.iag times in the salt
bath a."0. ~'nown Lr Figs and 6 (1~ and 2`0 sec. ~~espectively).
The i_u,e!2tigakic;_ 3!-:14'ad LI-at il~ relffystall.J.zition of
stilel (with a
4.-,ex.ura) tts greatest *probability
of' gen-:,tatio,7i p-'-s~s,_-6d ra,rys~a-
o
f-.,Il-r c:)-LjjIid3S Wit.,--~ that of
TL'A6 leads 'L.3 the first
tr,=_ _-,Of~.Imation The
no:mally observed in the
appears late-r in t'e
Card 2/3
The rates :,f heating

."OV/180 -59-1-21/2r)
Investigation of the Orientation of Recrystallization Centres at
High Rates of Heating
used had no appreciable effect on the mechanism of the
formation of new grains on recrystallization.
There are 6 figures
Soviet and 2 French.
SUBMITTED: August 7, 1958
and 7 references, 5 of which are
Card 3/3

66389
12-ID SOV/58-59-10-22722
_T:--r-slation from. Referativnyy Zhurnal,
Fizika, 1959, Nr 10, PP 134 - 135 (USSR)
AITT ORS, Gaydukov, M.G.,
Creep of Aluminum-Magnesium and Nickel-Copper Solid-Solution Alloys
'E7-10DI~_-AL- Tr. In-ta fiz. metallov. AN S3SR, 1959, Nr 22, Pp 107 - 112
ABSTRk7f- The authors studied creep in AI-Mg alloys at temperatures of 1500 to
4000C and stresses of 2 and 0.3 kg/mm2, and in Ni-Cu alloys at
temperatures of 5000 to 7000C and stresses of 5 and 2 ka/c=2. They
established that the solid-solution concentration dependence of the
creep rate varies with a variation in temperature and active stresses
This Is explained from the point of view of a variation in the ratio of
participation of shearing and diffusion mechanism of plastic defomatloL
under various conditions of deforming.
The authors' r6sumb

24(6), 18M SOV/126-?-2-14/39
AMMORS: Gaydukov, M. G. and Pavlov, V. A.
TITLE: Dependence of Creep of Al-Mg Alloys on Temperature and
Applied Stress (Zavisimost' polzuchesti splavov Al--Mg
ot temperatury i velichiny prilozhennykh napryazheniy)
PERIODICAL: Fizika Metallov i Nietallovedeniye, 1959, Vol 7, Nr 2,
pp 254-258 (USSR)
ABSTRACT: Alloys of Al (99.99% purity) and 0.12, 1.11 and 2.20% ML,
were made in a high frequency furnace. The ingots were
forged into rods, from which specimens were made 9 with a
working part length of 50 mm, a diameter of 8 mm, and
threaded ends. In order to ensure an equal grain size
for all alloys (0.16 mm.), the specimens were annealed
at temperatures specially selected for each alloy in the
temperature range 440-4600C. Theotemperature was kept
constant automatically within + 2 Ct and was measured
by two thermocouples attached To the specimen. The
duration of testing was up to 200 hours. In Figs 1 and
2, creep curves for pure aluminium and an aluminium alloy
containing 0.12% Mg are shown, from which it can be seen
that alloying of Al with even a small quantity of M6
considerably increases its strength. The strength
Card 1/3 increases further with increase in Mg content. This can

SOV/126-7-2-14/39
Dependence of Creep of Al-Jjig Alloys on Temperature and Applied
0
Stress
be seen from the creep curves of Fig 3. In Fig 4 the
change in the logarit4 of the creep rate with chanre in 2
composition at 150-350 C and an actinG stress of 2 k~;/mm
is shown graphically. In Fig 5 curves for the change in
the loGarithm of the creeg rate with concentration o5 the
solid solution at 250-400 C at a stress of U.3 kg/mm are
shown. Comparing the curves of Figs 4 and 5, it can be
seen that as the deformation stress changes, the
dependence of the strenUth of alloys on concentration
changes considerably. From the above experiments the
authors have arrived at the following conclusions:
1. As a result of alloying aluminium with ma-nesium, the
greatest strengthening of alloys is observed when the
plastic deformation mechanism is a shearinG one.
2. At low deformation rates and relatively high
temperatures, the effect of strengthening the alloys
decreases considerably due to development of diffusion
plastic deformation, which is associated with the
diffusion of magnesium atoms under the action of heat
Card 2/3 and the deformation stresses applied.

SUV112~--7-2-141;~q
Dependence of Creep of A1416 Alloys on, lemipera-.-.~-r,~~ az~-d A;~;~iiet
Stress
There are 5 figures and 11 references, 7 of which are
Soviet9 4 English.
ASSOCIATION: Institut fiziki metallov A14 SSSR
(Institute of 11.1etal Physics, Ac. Sc. USSR)
SUMITTED: June 1U, 1958
Card 3/3

/?- 1.?150
67719
AUTHOM Noskova, N. I. and Pavlov, V. A. SOV/126-7-3-15/44
TITLE: X-Ral Stu(.?Of DistortioniPand Bond Forcs~~In the crystal
Lattieo%iof Nickel-Base Solid Solutionsti(Rentgano-
graficheakoys izuch9niy9-Ts-Fs-zh*niy I ail svyazi
kristallicheakoy reahetki tverdykh rastvorov na oanove
nikelya)
PERIODICAL: Fizika metallov I metallovedeniye, Vol 7, Nr 3, pp 400-
404 (USSR)
ABSTRACT: In this work static and dynamic distortions caused by
alloying have been measured in relation to heat treatment ani
plastic deformation, and the block formation and secondary
distortions In the deformed stato have been determin*d.
Solid solutions obtained by alloying nickelij(99.99%) with
Acopper (99.95%) and~61uminium (99.9-UTT-were studied.
The composition of the solid solutions inVestigated Is given
in Table 1. All solid solutions ware, melted in a vacuum
furnace. The static and dynamic distortions were determined
by a method described in Refs.7 and 8. The block size and
th* extent of secondary distortions in the deformed state
were determined by a method similar to that applied by lysak
Card 1/4(Refs.9 and 10~ The method of preparation of the specimens ~Z

67719
SOV/12& - r7-~,-l r- /4-4
X-Ray Study of Distortions and Bond Forces in the Grystal Latticto of
Nickel-Base Solid Solutions
for investigation has been described in Ref.2. The results
of a study of the fine structure of solid solutions of nickel
with 10, 20p 40 and 60% Cu are partly published in Ref.2.
The characteristic temperature, and the magnitude of static
and dynamic distortions of the crystal lattice of' these
solid solutions are given In Table 2. The nickel-aluminium
solid solutions in powder form were annealed prior to
Investigation. The annealing specifications are indicated
in Table 3. Subsequently the static and dynamic distortions
of the crystal lattice and the characteristic temperature
were determined. The results are given in Table 3. The
physical nature of hardened one-phase solid solutions is
not absolutely clear yet. In the present work the Jx.fluence
of plastic deformation on the fine structure has been studied
by deforming the above solid solution by filing at room
temperature. This method of deformation has been chosen
for Its convenience for X-ray Investigation. Specimens
were made from the powder for taking X-ray pictures by
Card 2/4 the Debys method. X-ray pictures were taken at room

6771~
O',OV/l26--7--3--15A4
X-Ray Study of Distortions and Bond Forces in the Crystal Lattice of
Nickel-BRBe Solid Solutions
temperature and at the temperature of liquid nitrogen with
the aim of establishing the eharacteristic temperature of
the specimons in the deformed state. X-ray picturea were
taken of annealed and deformed specimens In K,,,-molybdenum
irradiation. Besides the sooondary distortions and the
block size in deformed specimens of nickel-aluminium,solid
solutions were also determined by exposure to
irradiation. The results of the investigation are Ohown in
Table 4. As a result of the above experiments the authors
arrived at the following conclusions.
1. When solid solutions form,by alloying nickel with lead
and aluminium,static distortions arise,the magnitude of
which Increases with alloying (within the range of the
additions Investigated). The characteristic temperature
rises on alloying nickel with aluminium, and drops on
alloying nickel with copper.
2. Plastic deformatio *(by filing) at room temperature
lowers the characteristic temperature of nickel alloys
containing 2.93% aluminium, but raises It in a nickel
Ca-rd 3/4 alloy containing 40% copper.

67719
SOV/126-7-3-151/44
X-Ray Study of Distortions and Bond Forces in the Crystal Lattice of
Nickel-Base Solid Solutions
3. For under-load processes the possibility of raising
or lowering the characteristic temperature must be taken
into consideration.
There are 4 tables and 14 references, of which 11 are Soviet,
1 English and 2 German.
ASSOCIkTIOE: Institut fiziki metallov AN SSSR (Institute of Physics
of Metals, Ac. Be., USSR)
SUBMITTED: July 23, 1958
Card 4/4

si, 0 66231
OD I /?I "? SOV/126-8-3-15/33
AUTHORSs Pavlov, V.A. and Fereturina, I.A.
TITLE: Mechanical Properties of Nickel-Aluminium Alloys
PERIODICAL:Fizika metallov i metallovedeniye, 1959, Vol 8, Nr 3,
PP 417-425 (USSR)
ABSTRACT: In the present work results are given of an investigation
of the relationship between the UTS on the one hand and
alloy composition and conditions of deformation on the
other, of nickel-aluminium solid solutions. These
alloys are characterized by the fact that their modulus
of elasticity, characteristic temperature and static
distortion of the crystal lattice increase with increase
in alloy concentration. A considerable part of the
increase in interatomic bond force appears to be
associated with the existence of close order, as during
plastic deformation at room temperature the characteristic
temperature decreases, approaching the value of pure
nickel (Rof 3). The alloys were melted from the high
purity electrolytic nickel NOOOO and the alutninium AVOOO
in a vacuum of 10-5 mm Hg. The ingots were homogenized
and forged into rods, 10 x 10 nim. The billets were
Card 1/4 planed to a depth of 0.5 to 1.0 mm in order to remove the
LIK

66231
SOV/126-8-3-15/33
Mechanical Properties of Nickel-Aluminium Alloys
surface layer and subsequently rolled and drawn into
wires of approximately I nini diameter. Wire drawing was
carried out at room temperature with the application of
several intermediate annealing treatments in vacuum at
3009C. After the last intermedinte anneal, the wirco wore
given a deformation of 80% reduction in area and iti this
state were allowed to recrystallize in the temperature
range 85U to 1000*C in vacuum. The recrystallization
temperature for each alloy was selected so as to ensure
equal grain size for all alloys. The linear grain size
in all alloys was approximately 0.1 min. The specimens
were pulled in a special machine and the temperature was
var4ed front 77 to 973*K. The deformation rate at the same
time increased 300 times. Fig I shows tire curves for the
temperature dependence of the UTS of pure nickel and
nickel alloys containing 0.025, 0-05, 0.5, 1.5 and
2-93% Al. Fig 2 sliows curves for tite dependence of tho
UTS on the c uric entrat ion of the solid solution for two
deformation rates, differing by a factor of 300. Fig 3
shows the difference in UTS at -196 and 100*C varyin8 w.Ltl-i
Card 2/1* Al content. Fig 4 siiows a curve for the change in UTS in
L4-

66231
sov/126-6-3-15/33
Mechanical Properties of Nickel-Aluminium Alloys
relation to the reciprocni of tomporature for -low
temperatures of deformation (from 77 to 6000K). The
authors arrive at the following conclusions-. On alloying
nickel with aluminium, the solid solution increases in
strength except for low concentration regions in which an
initial decrease in UTS is observed. As the concentration
of the solid solution increases, the dependence of the
UTS on temr,crature and deformation rate increases. In
alloyB containing 1.5 and 2.93%A1, an uneven relationship
between UTS and temperature exists. The experimental
results of the present work, as t1jose of investigations
of other alloys in preceding papers, show that tlie chief
reason for the strengthening of alloys on plastic
deformation by slip is a change in the nature of the
fine structure of the solid solution, which leads to a
fuller employment of the interatomic forces in the band.
The fact that UTS is dejendeiit to a greater measure on
temperature and deformation rate in the case of alloys
than it is in that of pure metals, anu also t,"ie uneven
temperature dependence, show that in the investigated
Card 3/4 solid 5olutions thermally activated processes occurring
~'K

66231
SOV/126-8-3-15/33
Mechanical Properties of Nickel-Aluminium, Alloys
during deformation influence the develol-ment of
plastic deforwation by slip. There art, II figures anti
21 refere"ces, 6 of which are Soviet and 15 Western.
ASSOCIATIONtInstitut fiziki metallov AN SSSR (Instituto ot Metal
Yhysics AS USSR)
SUBMITTED: August 21, 1958
Card 4/4

. 1A / -21S-0 / /,P. Pd 0 0 66232
AUTHORS: Gaydukov, Y.G. and Pavlov, V.A. SOV/126-8-3-16/33
TITLE: Dependence of Creep or Nickel-Copper Alloys ort Solid
Solutiou Concentration and Deformation Conditions
PERIODICAL:Fizika metallov i metallovedoniye, 1959, Vol 8, Nr 3,
pp 426-433 (USSR)
ABSTRACT: The aim of the present investigations was to study tho
influence of change of concentration of nickel-copl.or
alloys on their creel) bohaviour under conditions when
plastic deformation occurs preferentially, either by
slip or by a diffusion mechanism. Nickel-copler alloys
-ere made at the Special Alloys Laboratory of the
Institute of Metal Fh sics in a high frequency furnace
under a vacuum of 10-~ mm Hg. Electrolytic nickel
NOOOO (99.99010 Ni) and electrolytic copper with a total
impurity content of less than 0.05% (among them 0.02!6
oxygen) were the starting materialso Nickel and coyper
were first re-melted in vacuum in order to remove gases.
The ingots were forged into rods of 18 mm diameter, from
which specimens with threaded heads were ground. The
diameter of the working part of the specimens was 6 mm
Card 1/4 and the calculated length 50 mm. The specimens were

66232
Dependence of Creep of Nickel-Copper Alloys
Concentration and Deformation Conditions
Card 2/4
SOV/126-8-3-16/33
on Solid Solution
annealed at specially selected temperatures in the rarige
800 to 9000C in order to obtain approximately equal
grain size in all alloys. Testing was carried out oij
TsKTI-2 machines. During testing, the teini.erature was
kept constant within 2'0 and was measured by two
thermocouples affixed to the specimen. The taaie of
testing reached 500 hours in individual cases. Ili oraer
to study the behaviour of alloys under conditions ut
deformation by slip and by diffusion, arilrupriate
temperatures and deforniation stresses were beiected. Ili
order to ensure a preferential plastic del-ormation by slij,
during creep, tests were carried out at velati-vely low
temperatnres and high deformat-Lon stres,,~(,s. Prefuroittiai
plastic deformation by diffubion could be ensured by
using high temperatures and low stresses. The vaiues of
UTS of yure nickel and Ni-Cu allo)vs are ~howii in t:ie taL~e
on p 428 (Ref 9). 13, Fi,9 1 to 3, curveb arro show,, I'Or the
chotngo in deformation, obtuitiod at Llio munient of' ioadjL(q,
and after definite cruep time intorvnIti, witii it,
alloy coitcentration f*ur a tenijerature of' 5LC*C and W.It I~K

66232
SOV/126-8-3-16/33
Dependence of Creep of Nickel-Copper Alloys on Solid Solution
Concentration and Deformation Conditions
Card 3/4
stresses of 5 kg/mm 2 (Fig 4). From the results of
testing of several specimens of each alloy unaer
identical conditions (testing temperature and stress)
the average deformation rates in the steady portion of
change in acting stresses (9, 2 and 5 kg/mm 2 respectively).
Similar curves are obtained at 6000C at deformation
rne creep curves were cajLcuiateu.
results are plotted within
Ig deformation rate.- alloy
of 500, 600 and 700 C and two
In Fig 8, the values of external
after relaxation for 84 hours
initial stresses a. (2 and
The authors arrive at the following
(1) The creep rate of Ni-Cu
range 500 to 7000C depends
alloy and the conditions of
relatively low teml,eratures
commensurate with UTS, at waich
occurs preferentially by the
in r ig u anu L n e 13 e
the coordinates
composition, for temperatures
deformation stresses.
stresses persisting
are plotted against two
4 kg/mn12 respectively).
conclusions:
alloys in the temperature
on the composition of tho
deformation. (2) At
and high deformation stresses,
deformation most probably
slip mechanism, the creep

66232
SOV/126-8-3-16/33
Dependence of Creep of Nickel-Copper Alloys on Solid Solution
Concentration and Deformation Conditions
rate is inversely dependent on the UTS. The higher the
UTS, the lower the creep rate. Under these cunuitions
of deformation, alloys containing 40% Cu y,ossess the
greatest strength. (3) At high temperatures and
sufficiently low deformation stresses (stresses
considerably lower than the UTS) diffusion yrucesses
occurring under the influence of stress play the decisive
role. In this case the creep rate increases with
increase in the concentration of the solid solution.
(4) in a general case the behaviour of alloys under load
is determined by the extent to which each of the two,
plastic deformation by slip and that by diffusion, are
involved. There are 8 figures, 1 table and
12 references, 8 of which are Soviet, 3 German and 1 French.
ASSOCIATION:Institut fiziki metallov AN SSSR (Institute of Fletal
Physics AS USSR)
SUBMITTED: August 2, 1958
Card 4/4

66233
)'S-0 0 SOV/126-8-3-17/33
AUTHORS: lzbranov, F.D., and Rodigin, N.M.
TITLE: Some Peculiarities of Transformer-Steel RecrystalliZation
During Rapid Heating. 11. Kinetics of Texture Formation
PERIODICAL: Fizika metallov i metallovedeniye, 1959, Vol 8, Nr 3,
Vp 434-439 (USSR)
ABSTRACT: Much work (Ref 1 to 8) on recrystallization, particularly
that of transformer steel, has been carried out on
specimens subjected to isothermal recrystallization
annealing for times occasionally as long as several hours.
The object of the present work was to study the formation
and development of the recrystallization texture of
transformer steel at high heating rates. A steel with
3.54% Si with a reduction of 75 or 95,"' was used.
15 x 100 x 0.25 mm specimens were heated by an electric
current without holding; others, 0.11 mm thick, by
immersion in a salt bath at the required tenperature.
The electric heating was effected in the aplaratus
designed by N.M.Rodigin (Ref 10). The microstructure and
texture of recrystallized specimens were studied, using
a special camera, enabling the specimen to be disl,laced in
Card 1/3 two mutually perpendicular directions during exposure. ~X

66233
SOV/126-8-3-17/33
Some Peculiarities of Transformer-Steel Recrystallization During
Rapid Heating. 1I& Kinetics of Texture Formation
X-Ray patterns obtained are shown in Figures I to 4 and
6 to 9, and the microstructure in Fig 5. The authors
draw the following main conclusions. Two types of
texture arise in the recrystallization of transformer
steel. For the highly deformed material, the texture of
the first stage of recrystallization conforms to the
pronounced deformation texture; later this is replaced
by the texture generally found in isothermal annealing of
transformer steel. The heating rates (840 to 1170*C/sec)
and current densities used had no appreciable effect on
the mechanism of formation of now grains as regards
orientation factors. The high recrystallization rates
obtained by both methods of heating can be attributed -to
the considerable reduction in relaxation before
recrystallization and, possibly, also to the redistribution
of impurities. on rapid electric heating to temperatures
over 1000*C, the texture produced is substantially the
Card 2/3 some as the recrystallization texture in isothermal

OV. // 9/ 67695
op. ?~ -0 0 a-OV/126-8-4-17/22
AUTHORS: Izbranov, P.D., and Rodigin, N.H.
TITLE: Some Peculiarities of Transformer 3teell?Recrys tall i za tiorft/
on RaplA Heating. III. Depende-n-c-e-o-rthe Rate of Gra
Growth%'sand Activation Energy of this Growth on the 9-ate
of Heating 6
PERIODICALs Fizika metallov i motallovedeniye, 1959, Vol 8, Nr 1+,
pp 607-612 (ussw
ABSTRACT: The high rates of recrystallixation of cold-deformed
metals, particularly transformer steels on rapid heating
has been explained (Refs 1, 2) in terms of a change in
the condition of the metal before recrystallization.
This should affect the rate and activation energy of
grain growth and it was the object of the present work
to determine these parameters for both rapid and slow
heating of transformer steel and compare the results
together and with published (Refs 3-6) work in this field.
The steel used contained 0.08% carbon, 3 51+% silicon,
"v manganese, 0.018% sulphur, and 0 .1 % chromium.
0.15, 6
Card For rapid-heating experiments the material is subjected
to mechanical and heat treatment to give an average grain
1/3 size of 2-3 mm and a reduced number of recrystallization q'_1__

67695
SOV/126-8-L~-17/22
Some Peculiarities of Transformer Steel Recrystallization on Rapid
Heating. III. Dependence of the Rate of Grain Growth and
Activation Energy of this Growth on the Rate of Heating
centres. This involved 40% reduction of the initially
0.5 mm thick strip, followed by 2-3% cold reduction and
a further small (given 10% elongation) cold reduction.
The specimens were subjected to electric heating to
various temperatures (1000-1360 OC) and then air cooled.
The average size of the ten largest isolated grains
produced in the recrystallization was determined. This
is plotted against heating temperature in Fig 1, while
the logarithm of grain size is seen to be linearly
related (Fig 2) to the inverse of absolute temperature.
The activation energy is 13500 t 2500 cal/mol. The
temperature is shown in Fig 3 as a function of heating
time. Another series of experiments was carried out
with slow heating; the specimens, prepared as before,
being heated after 10% deformation in an ordinary furnace
to 870 OC at 0.20C/second and then annealed in a salt
Card bath at that temperature for 1+5 minutes. The average
2/3 size of the 20 largest isolated grains was determined and
the samples werp than no-i- -nn-sl-cl 0 r7 n r) ri Z.

#3 7 u9 5
SOV/126-8-4-17/22
Some Peculiarities of 'fransformer Steel Recrystallization on
Rapid Heating. III. Dependence of the Rate of Grain Growth and
Activation Energy of this Growth on the Rate of Heating
15 minutes and the grain-size redetermined. The rate
of growth at this temperature was determined from the
difference. The experiment was repeated at 900, 942,
and 975 OC. From a plot of the logarithm of the rate
of growth against inverse of absolute temperature, an
activation energy of 44000 cal/mol is obtained; allowing
for an experimental error of � 25% the minimum value is
33000 cal-mol, i.e. more than double the activation
energy for rapid heating. The growth-rate values for
the different temperatures for rapid and slow heating
are tabulated, and their ratio is plotted against
Card temperature in Fig 5.
3/3 There are 5 figures, 1 table and 7 references, of which
5 are Soviet, 1 is English and 1 is German.
ASSOCIATION: Institut fiziki metallov AN SSSR
(Institute of Physics of Metals, Ac.Sg. USSR i
Sverdlovskiy gosudarstvennyy pedagogicheskiy institut
(Sverdlovsk State Pedagogical Institute)
SUEMITTED: January 25, 1959 ~X

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4

S/1137/61/000/005/C)42/060
A006/A106
AUTHORS: Datsko, 0. 1., and Pavlov, V. A.
TIM- Temperature dependence of internal friction of pure nickel
PERTODICAL: Referativnyy zhurnaLl. Metallurgiya, no. 5, 1961, 32, abstralA 5Zh244
(V sb. "Relaks. yavleniya v metallakh I splavakh", Moncow, Metallurg-
Iz izdat, 1960, 234-240)
TM: The wathors review studies on the effect of grain boundaries on
intemal friction in metal and present, results of their investigations ork the
internal friction of Ni containing 19 0.013% Impurities. The ingots were forged
Into rods from which 0.80 = diam. wire was produced by rolling and drawing at
room temperature with Intermediate annealing. (Deformation after final axnealing
attained "). The temperature dependence of internal friction was studied with
the aid of a twisting pendulum, in a vacuum at about 0.5 cycles oscillation
frequency. Thq deformed specimens were heated several times to different tempera-
tures and internal friction was determined after each heating. A strong depend-
ence of attenuation from the coLdItione of me_~hanlaal and thermal treatment was
established which indicates that plastic deformation of a specimen causing the
Card 1/2

GAYDUKOV, M.G.; PAVLOV, V.A.
Dependence of creep in nickel-copper alloys on the concentraticn of
solid solutions and deformation conditions. Isel. po zharopr. splav,
6:64-70 060. (MIRA 13:9)
(Creep of metals) (Nickel-copper alloys-Metallography

0 0 S/126AO/009/0;~/015/0-,
AUTHORS: Pavlov, V.A. and Pereturina, 1
TITLEt Alloying_ Additions on the Valu- 'I"
Temperature Der-endence of the Yield Point
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol 9, Nr '2,
pp 248 - 257 (USSR)
ABSTRACTi A discussion of results of previous investigotions anci
of some new experimental data obtained. on nickel aiik~
cobalt alloys is given. As inearlier work, the
temperature dependence of the yield point of alloys is
more complicated than that of pure metals. The position
of the maximum on the temperature-yield point curves of
alloys depends on the concentration of the alloying
element and the rate of deformation. The change in
character of the curve for alloys compared with pure
metals cannot be explained by changes in interatomic
bond strength. Experimental data and theoretical
considerationo indicate that the influence of alloying
additions on the mechanical. properties is due to inter-
action between dislocations and atoms or groups of ILMIS
Cardl/3 of the alloying element, which reduces the mobility of q1""

68627
s/126/6o/oo9/o2/0l5/033
IIIJ14P-335
The Influence of Alloying Additions on the a u nd Temperatu,,
Dependence of the Yield Point
the dislocations and sometimes increases the voltame of'
metal taking part in deformation. This increases the
efficiency of use of the interatomic bond strength. The
influence of admixtures on the resistance to deformation
can be explained qualitatively by assuming that there is
(according to Cottrell and Suzuki) a relation between the
dislocations and the atoms of the admix,%Iures, that there
are non-uniformities in the concentrations of the type K
state and also a redistribution of the atoms in the stress
field with mobile dislocations according to shock. The
strongest influence is shown by additions which cause
static distortions in the original crystal lattice. 'In
nickel-cobalt alloys, where the static distortion cau.sed
by the cobalt is small, the strengthening is due to
ordering. Acknowledgments are expressed to A.N. Orlov
for his comments.
There are 5 figures and 35 refere.nces, 15 of which are
English, 3 German and 17 Soviet.
Card 2/3

80222
S/126/60/009/04/029/033
/A )'5-'VV E021/E435
AUTHORS: lzbranov, P.D., Rodigin, N.M. and Pavlovt V.A. IgI
TITLE: The Orientations of the Centres ot 11ec`7?S"?TY"%1fion at
High Rates of Heating
PERIODICAL: Fizika metallov i metallovedeniyes 1960, Vol 9, Nr 11,
pp 63o-633 (USSR)
ABSTRACT: To investigate the influence of high rates of heating
on the distribution of the new grains, experiment
recrystallization of samples of a transformer ste:,?Zere
carried out. The rate of heating was 2000OO'C/sec,* which
was made possible by using special equipment described
in an earlier paper by one of the authors (Ref 3).
Samples were prepared from cold rolled strip with 97%
deformation. The recrystallized samples were
investigated by metallographic and X-ray analysis.
Fig I shows an X-ray photograph of the cold-worked sample,
Fig 2 of the recrystallized sample, Fig 3 shows the
equiaxed grains of the microBtructure of the
recrystallized sample. Comparison of Fig I and 2 shows
that, in the main, the new orientations of the new
Card 1/2 crystals correspond to the orientations in the cold-worked

XMVA, V.P.; PAVIOV, V.A.
Mrfect of elastic waves on internal friction at low temperatures in
aluAnum alloys with 2 percent magnesium. Piz. met. i metalloved.
10 no.3:445-452 S 160. (MIRA 13:10)
1. Institut fiziki metallov AN SSSR.
(Aluminum alloys-Testing) (Internal friction)

,2,1 ~%Al Do ?,SOB 1,521 1191 E5920 S/126/61/012/001/012/020
tt i2 E193/E48o
AUTHORSi Pavlov* V.A., Gaydukov, M.G., Noskova, N.I.
Mellniko-va, V.V.
TITLE: The role of slip and diffusion in plastic deformation
during creep of nickel-copper alloys
PERIODICALt Fizika metallov i metallovedoniye, 1961, V01.12, No.1,
pp-97-107
TEXT: This paper was presented at the session of the Nauchnyy
8ovet po probleme prochnosti i plastichnosti. tverdykh tel AN SSSR
(Scientific Council on the Problems of Strength and Plasticity of
Solids AS USSR) in June 1960.
Slip or diffusion constitute the two possible mechanisms of plastic
deformation. No agreement has been reached regarding the
mechanism of plastic deformation in creep. According to one
school of thought represented by S.N.Zhurkov, the diffusion
processes play no significant part in plastic deformation in creep,
an opposite view being held by the other sr-hool of thought
represented by B.Ya.Pines. Since both these opinions are based on
experimental data, the most likely explanation of this apparent
contradiction is that either mechanism can operate depending on the
Card 1/8

s/126/61/012/001/012/020
The role of slip and diffusion ... 9193/E480
conditions of stress and temperature, and the object of the present
investigation was to study the effect of these two factors on tile
mechanism of plastic deformation in creep of Ni-Cu alloys. The
Ni-Cu sy3tem was chosen for this purpose because (a) an incretise in
the Cu content in Cu-Ni alloys brings about a decrease in the
elastic modulus and the characteristic temperature of these alloys
and an increase in the magnitude of the static distortions of the
crystal lattice and (b) the activation energy for diffusion of
copper in nickel is almost 1.5 times higher than that for self-
diffusion of pure nickel, the former amounting to 35000 to
40000 Cal/mol. These data indicate that the addition of Cu to
Ni decreases the interatomic bond forces and, consequently,
increases the intensity of the diffusion processes. even at
relatively low temperatures. The vacuum-melted experimental
alloys, containing 10, 20, 40 and 60% Ni, were prepared from
99.99% Ni and electrolytic copper containing less than 0.05%
impurities. The ingots were forged into 18 mm diameter rods from
which the test pieces, 6 mm in diameter and 50 mm (for creep tests)
or 100 mm (for stress relaxation tests) long, were prepared.
Card 2/8

25920 S/126/61/012/001/012/020
The role of slip and diffusion ... E193/9480
These were annealed at 800 to 9009C, the annealing temperature for
each alloy having been selected so as to obtain the same grain-size
(approx. 0.1 mm) in all test p eces. The rate of plastic
deformation varied between 10-t and 10-11 (sec-1). In the first.
tage of the investigation, the effect of alloy comp?sition and
xperimental conditions on the rate of deformation r was studied.
:
The results relatin to steady creep are reproduced in Fig.1,
where log i (sec-1) i;/plotted against the Cu content W in
the alloys tested at 5 k mm2. The test temperature is
indicated by each curve. In Fig.2, 109 i (sec-1) is plotted
Against the Cu content W in alloys tested at 600*c, the magnitude
of the applied stress (2 and 9 kg/mm2) being indicated by each
Curve. In the next stage of the investigation the relationship
between the applied stress o and the activation energy Q of the
deformation process was studied, The results are reproduced
graphically. In Fig.5, Q (kcal/mol) is plotted against
a (kg/MM2), the experimental points denoted by crosses~, circles
nd dots relating, respectively, to pure nickel, 40% Cu-Ni alloy
:nd 60% Cu-Ni alloy. In Fig.6, log i (sec-1) is plotted against
lo3/T (where T is the absolute temperature) for the 40% Cu-Ni
Card 3/8

S-*126/61/012/001/012/020
The role of slip and diMPion ... E/193/E480
Q - YO
i = ioe RT
High activation energy and the fact that the above relationship is
valid for low temperature and high rates of deformation Indicates
that under these conditions plastic deformation in creep takes
place predominantly by the mechanism of slip. (3) Under conditions
of high temperature and low applied stresses, the activation energy
for the deformation increases with decreasing stress and approaches
the activation energy for the diffusion of the alloying element.
In this case the process of deformation In zreep can be described by
the known equation for plastic deformation by diffusion:
Dcya3
FkT
Under these conditions of deformation the strength of alloys
decreases and may be lower than that of unalloyed metal which
indicates the predominance of the diffusion mechanism of deformation.
Card 5/8

Z592o S/126/61/012/001/012/020
The role of slip and dif-fusion E193/E48o
(4) In the intermediate region of temperature and stress, plastic
deformation by slip takes place aide by side with the diffusion
relaxation process. The results of X-ray analysis indicate that
under these conditions the plastic deformation brings about
fragmentation of the crystals and formation of blocks, In this
case the deformation in creep is approximately described by the
formula due to J.J.Weertman (Ref,28~ J.Appl..Phys., 1955, 26, 1213)
; - C (cia/RT] exp (- Q/RT)
There are 12 figures, 3 tables and 28 references. 18 Soviet and
7 non-Soviet. The four most recent references to English language
publications read as follows; Ardley G.W. Acta met,, 1955, 3, 525;
Greenough A.P. Phil. Mag., 1958, 3, 1032; McLean D. Inst.Metals,
1952-53, 81, 287; Weertman J. J.Appl.Phys,, 1955, 26, 1213,
ASSOCIATION: Inatitut fiziki metallov AN SSSR
(Institute of Physics of Metals AS USSR)
SUBMITTED: December 22, 1960
Card 6/ 8

S/126/61/012/004/011/021
Elll/E335
AUTHORS: Noskova, N.I. and Pavlov,--V.'A*
TITLE: X-ray-diffraction study of the fine structure of
nickel iron after y--a and y-a-y transformations
PERIODICAL;, Fizika metallov i metallevedeniye, v. 12, no. 4,
1961, 580 - 582
TEXT: The authors point out that polymorphic, changes
contribute to the prodijction of the strengthened state in
metals. The reverse poly-morphic transformation (alpha-to-
gamma iron) has been insufficiently studied because of experi--
mental difficulties and little information is available on the
structural changes produced inside grains. Although biock
disorientation has been studied (Ref. 4 - Edmondson, Acta met.,
1954, no. 2, 235). there is as yet no detailed picture on the
fine tructure after reverse tran~iformation. The authors study
block size and type Il distortions in the present work, as a
result of forward and reverse transformation of nickel iron
(0.04% C, 0.38% S1. 0.33% Mn 0.51% Cr, 28.23% Ni and remainder
Fe). The temperatures of the martensite transformation and the
Card 1/~

s/126/61/012/004/0.11/o2i
X-ray-diffraction study of EIII/E335
end of reverse transformation are -20 and 580 0C, respectively.
Powder was used for the X-ray investigation, prepared by filing
a rod, previously annealed at 1 100 0C, for-30 min. After 0
sieving, the powder was vacuum-annealed (10 mm Hg) at 1 100 C
for 30 min and vaauum-cooled at 100 0C/min to room temperature V/
and quenched in liquid nitrogen. The quenched powder was divided
into two halves, each of which was vacuum-annealed for 1 hour at
100, 200, 300, 400, 500, 580, 6oo, 700, 900 or 1 100 0C and re.-
sieved. Cylindrical specimens, 0.7 mm diameter, were prepared
from the powder and subjected to X-ray diffraction in a 150-mm
diameter camera with Ka-iron radiation. The width of (111) and
(222) diffraction lines of austenite and (110) and (220) of
martensite were measured from photometry results, corrections
being applied whichwere based on the method of Lysak (Ref. 7 -
FM, 1952, no. 3, p-28; 1955. no. 6. p. 40; 1954, no- 5,
p. 45). The studied line width for alpha-iron was obtained
from nickel-iron filing0produced under nitrogen and then
vacuum-annealed at 400 C for 3 hours; for gamma iron - from
filings vacuum-annealed at 1 100 0C for 30 min. The results
Card 2/3

0. 1300
32657
s/126/61/012/005/017/028
E091/E335
AUTHORS: Pavlov, V.A,, Gaydukov, M.G. and Mellnikova, V-V.
TITLE; Nechanis-m-o-1-plastic defori-iiation in the creep of
aluminium-mignosium alloys
PERIODICAL: Fizika metallov i metallovedeniye, v. 12, no. 5,
ig6i, 748 - 755
TEXT: Pare aluminium and aluminium alloys containing 0.1,
I and 2c Mg were investigated. The alloys were melted under flux
_~h
in a hi -,frequency furnace. The ingots were forged into rods of
18 mm diameter, from which specimens 50 mm long and 8 mm in
diameter were made for creep-testing and other 100 mm long and
8 mm in diameter for stress-relaxation testing. The specimens
were annealed at 420 - 440 OC. Foreach alloy, the annealing
temperature was selected so that a linear grain diameter of 0.1
mm should be obtained. The rate of plastic deformation was
chosen within the limits 10- 4see- I to 10- losec-1. Rates below
10-8 sec-1 were obtained during stress-relaxation and the higher
rates in creep. The mechanism of plastic deformation could be
Card 1/~

32657
s/i,-,6/61/012/005/01'/028
Mechanis;.i of plaLitic E091/E335
of activation -..;'ith incrc~~se ii stresses in Cie alljys .151 the
di.ffusiori .iechanis.-.i of )IaFtic defor-~iiti3n ,rocees. S.N Z'iurLov
T-P Sanfirova, B.Ya. Pines and A.F. Sirenho are ;,ientioned 3.11
the article in connection wit:i their contributions in tI-)is fa,ald,
There are 11 figures I table and 18 references: 14 Sovi et -1) L Oc
and 4 non-Soviet-bloc T!ie four En,~~Iish-lan_-uage ref ereiic es
mentioned are, Ref~ 9~, F.R. Nabarro - Rep. Conf, Stren-crt!i of
Solids, L 1948, 75, Ref. 10: C.J. Herring - J. Appl. Phys..
1950, 21, no. 5, 437, Ref. 11- J.J. Weertman - J. Appl. Phys.,
1955, 26. 1213; Ref, 18- F.11 Buttner, E.R- Funx, 11. Udin -
J Metals, 1952, It, 401.
ASSOCTATION, Tiistitut fizilu metallov AN SSSR (Institute of
P:ivsics of Metals of the AS USSR)
SUBMITTED Mal-C, 27 1961
\X
C"--C! V7)

S/126/6i/012/006/021/023
F-073/E535
AUTHORS~ Kuznetsov. R.I. and PavLo-v,--V,A.
TITLE Position of jumps on the extension diagram of poly-
crystalline tin
PERIODICALt Fizika metallov i metallovedeniye, v.12, no,6. 1961
919-921
TEXT; The authors investigated polycrystalline specimens of
99,999% purity tin of 2 mm diameter, 50 nun long with a grnin size
of 0.1 mm in the range from 2room temperature to -1000C and for
deformation rates at 8-10- to 2,lo-5 %/sec. A characteristic
featur.t of the diagrams is the presence of jump5, the location of
iflilch depends on the speed and temperature during the tests. With
a lowering of the temperature the region of the jumps shifts
towards the initial point of the diagram if the deformation rate
remains constant, At a constant temperature, the displacement is
in the same direction as the increase in the speed of deformation
Thereby, the nature of the jumps does not change, It was found
that the deformation E, which corresponds,to the first jump on the
extension diagram, the deformation speed C and the test
Card 1/3

Position of jumps on the S/126/61/012/006/021/023
E073/E535
temperature T are linked with the following relation;
C exp ~-QATI, where C and Q are constants, Plotting this
relation in the coordinates InE~ - I/T.a linear relation is
obtained and from the inclination of the straight line expressing
this relation the activation energy Qcan be calculated which is approx-
imately equal to 10 kcal/mol, which coincides with the acl.1vatior,
energy of seif-diffusion for tin, In view of the fact that the
material was of very high purity, it is difficult to visualize
that these jumps are associated with the presence of impiLrities -in
the metal- It can rather be assumed that their appearanLe is due
either to twining during deformation or to polymorphous trans-
formation of the tin from the P into OL-modification during the
process of deformation at a temperature which is below the
transformation temperature. i.e, below 18'C, There are 2 figures
and 12 referen.-es: 7 Soviet-bloc and 5 non-Soviet-bloz The four
latest English-language referencea read as followsi Ref.1 IchU K.
J.Phys,Soc_ Japan. 1959. 14, 12 ' 1822, Ref,2- Basinski Z_S_ Prot-,
Roy.Soc,. 1957, A240. 1221. 229, Ref,9 Zener C_ Hollmon. S_H_
Card 2/3

Position of jumps on the
J Appl~Phys, 1944. 15~ 22i Ref.10
Phil Mag.. 1952, 7, 43~ 422.
ASSOCIATION- Institut fiziki. metallov
(Institute of Physics
SUBMITTED: July 28. 1961
S/126/61/012/006/021/023
E073/E535
Thomson N- and MIllard D,S
AN SSSR
of Metals AS USSR)
Card 3/3

PHASE I BOOK EXPLOITATION sov/6271
Pavlov, V. A.
Fizicheakiye osnovy plasticheekoy deformatsil metallov (Physical
Principles of Plastic Deformation of Hetals). Moskva, Izd-vo
AN Sm. 1962. 198 p. Errata slip inserted. 3000 copies
printed.
S;Ionsoring Agency: Akademiya, nauk SSSR. Institut fiziki metallov.
Reap. Ed.: M. V. Yakutovich; Ed. of Publishing House: V. 1. Meder;
Tech. Ed.: V. M.Fremd.
PURPOSE: This book is Intended for scientific research workers
and engineers concerned with problems of metal physics and
metal science.
COVERAGE: The book reviews the principal physical laws governing
plastic deformation under conditions of the conventional tensile
tester creep. Data on the movement of dislocations in the re-
Card 1/7

Physical Principles of Plastic Deformation of Metals SOV/6271
gion of stresses are presented. Basic concepts of the mechanism
of plastic deformation are explained from the standpoint of
the th6ory of dislocations. The effect of alloying elements
on plastic-deformation phenomena in single-phase solid solutions
Is discussed on the basis of investigations conducted by the
author at the Institute of Physics of Metals, Academy of Sciences
USSR. In addition, views are expressed on the mechanism of
strengthening of single-phase solid solutions and on the mechan-
ism of plastic defoimation in creep. The author thanks Academi-
cian 0. V. Kurdyumov, S. N. Zhurkov (Corresponding Member,
Academy of Sciences USSR), E. S. Yakovleva, V. T. Shmatov,
M. G. Gaydukov, N. 1. Noskova, 1. A. Pereturina, V. V. Mellnikova,
V. P. Ketova, and A. N. Orlov for their assistance. Each chapter
is accompanied by Soviet and non-Soviet references.
Card 2/7

V JU/V ') 1z 19,;3
PHASE I BOOK EXPLOITATION SOi/6271
Pavlov, V. A.
Fizicheakiye esnovy plasticheskoy deformatsii metallov (Physical
Principles of Plastic Deformation of Metals). Moskva, Izd-vo
AN MR., 1962. 198 p. Errata slip inserted. 3000 copies
printed.
Inatitut fizlki metallov.
Sponsoring Agency. Akademiya nauk SSSR.
Reso.. Ed.: M. V. Yakutovich; Ed. of Publishing HoUse: V. 1. Meder;
Tech. Ed.: V. M.Fremd-
PURPOSE: This book Is intended for scientific research workers
and engineers concerned with problems of metal physics and
metal science.
COVERAGE: Itse book reviews the principal physical laws governing
plastic deformation under conditions of the.conventional tensile
testcr creep. Data on the movement of dislocations in the re-
Card lt~

Ph7alcal Principles of Plastic Deformation of Metals SOV/6271
gion of stresses are presented. Basic concepts of the mechanism
of plastic deformation.are explained from the standpoint of
the thdory Of.dislocations. The effect of alloying elements
on plastic-deformation phenomena in single-phase solid solutions
Is discussed on the basis of investigations conducted by the
author at the Institute of Physics of Metals, Academy of Sciences
USSR. In addition, views are expressed on the mechanism of
:strengthening Of single-phase solid solutions and on the mechan-
lam of plastic deformation in creep. The author thanks Academi-
elan 0. V. Kurdyumov, S. N. ZhurkoV (corresponding Member,,
Academy of Sciences USSR), E. S. YakovleVa, V. T. Shmatov,
M. G. Gaydukov, N. 1. Noskova, 1. A. Pereturina, V. V. Mellnikova,
V. P. Ketova, and A. N. Orlov for their assistance. Each chapter
is accompanied by Soviet and non-Soviet references.
Card 2/~

SRID62/014/001/008/o18
E193/E383
AUTHOR: Pavlov, V.A. and Pereturina, I.A.
TITLE: The effect of alloying additions on the mechanics
of plastic deformation of alloys and on the shape of
the stress/strain diagram
PERIODICAL: Fizika netallov J motallovedeniye, v. 14, no. 1,
1962, 92 - 98
TE=: The object of the work described in the present paper
was to analyze a large body of experimental data obtained by
the present authors and by other, both Soviet and foreign,
workers and to correlate data relating to pure-metals (Al, NO
and alloys (Al-DIS, Ni-Cu, Ni-Al, Ni-Co) in order to evaluate
the effect of alloying on some aspects of plastic deformation
a of metals. The first chapter is devoted to the temperature-
dependence of the yield point. The effect of alloying on this
A; relationship is demonstrated schematically in Fig. 1, where the
Aij yield point (cr) is plotted against temperature (T), curves 1
Th and 2 relating, respectively, to pure metals and alloys. The
or
Card 1/4
-Lj2dica -,4e PO 'lilt 94-0
ted -Y-'eld Of C7
by ea C Pojnt(Met a a
curlreo'
plotte(2

B/126/62/014/001/008/018
Tae effect of alloyinZ E.193/E383
amainst therCu content (01). The presence of a maximum on
urves of this type has been attributed to the refining
(purifyin-) effect of small alloying additions. Since, however,
the magnitude of this effect in Ni-Al alloys decreases with
increasing rate of strain (~r with decreasing temperature in the-
case of Ni-Cu alloys) it is obvious that it must be caused
by some other factors. Passing--on to the effect of alloyin&
additions on the shape of the true-stress/strain diagram, the
authors distinguish between two types of this diagram. In the
low-temperature type, the stress reaches its maximum near the
end of t:ie dia-ram (i.e. at high strain values) after vrhich it
decreases rapidly due to the onset of localizeddeformation
(necking); in the high-temperature type the maximum of the true
stress is reached near the beginning of the diagram (i.e. at low
strain values); after that the stress remains constant or slowly
decreases and finally falls down rapidly when the neck begins to
form. In all the systenis studied the introduction of alloyinz
elements raises the temperature at which the stress/strain
dia.t-ram changes from the low-temperature to the high-temperature
type. The addition of alloying elements increases also the value
Card 3/4

s/i26/62/ol4/ool/oo8/oi8
The effect of alloyinZ .... E193/E383
of stress 07 at -&-rhich the parabolic increase in the
resistance-t1ol-Lformation of strained metal begins. This
indicates a decrease in the energy of the stacking faults.
Tblere are 9 figures.
ASSOCIATION: Institut fiziki metallov AN SSSR (Institute of
Physics of Metals of the AS USSR)
SUBMITTED: July 29, 1961 (initially)
December 27, 1961 (after revision)
Fig. 1:
Card 4/4 7"

14 :11 11 f
Z193/E333
AUT71iC)-Z.'J: Javlov, V-A,, 71aydukov, M.G. and 'Mcllnilova, V.V.
TITLE: Jc,)cnde,ice oi' the r.;cchaiiisrii of pla:Aic doform.-Aion in
croci) of :i-Al and Ni-Co alloyp oil the conditions of
defor;;iction
PE.ZICDICAL: Fizi!-~- metallov 'i metallovedeniye, v. 111, no. V11
1962, 275
TLXT: In continuzition of their earlier work on the
of creo,, of :i-Cu anO. Al-:.:_- alloy!-,, the present authors inve.,;ti-
zated Cie effect of various factors on the mechanis:-.i oi~ croe,) of
Ni-Al zrnC ',-.i-Co alloys. Tlie Ni-Al alloys, cont'ainin~; up :o Al
i..roro c:io!~;cn as one of the materials because zhey
represe 'ited alloys charactcri.zed by relatively large st,-,t.Lc lattice
distortir);I!; alld 11011-taollotollic colic Critrat ioll-dopolidenc C of' the
olnstic Oclulus. I:i contrast, the lattice difitortions iii -'i-Cu
alloyt (-:it!i up to Go, Co) wore relatively small and their
olasti*c i:iodulus -aas )rzictically iri(Idpendent of the cot-.i;)ositio:l.
The crr-ep tests were carried out at 500 and 8oo 0C, the rate of
Card l/ 1i

Dopmidenco of .... E193/E383
-it -:_ -1
cr,.,o,, v:.-yiii:T beti-.rcen 10 ant! 10.'i ec i-,ie resul.t..,, --xe
re')roCaic c(-*. in t Ii e forn of Ir,).)hs , s:iowinf~ conc ent ration-
de:IOI-IC:C:'.C(- of the 1-;Itc of creel) un-er vz-.rious '11):)licd
rc1ntiouj'.iip between ":.c rate of creel) and the yield )uiiL;
stresz-(!o,)cndcnce of t:io activation oncrgy for creep of t:IC
alloy.-. !~tudicd; stress- and tei.i-)er;iturc-dcpendcicc of t;i(-
of creep. The conclitsiom can be sum iarizek, .-,s f 11 o--
1) Slin is the prec:o:iiinant ::iec!iariLi-.i of plaotic defor;,:iI, ~ ,-
creep at relatively low temperatures and high itressess. Th c
rclz,.tion!-'iip between the rato of creep under these conditi,):I
on the one hand, and temperature and stre.9s,on the other, ca;,, be
described by in expressioii due to Zhurkov and Sanfirova
(DAN SSSR, 1955, 101, no. 2, 257):
Q-Ya
RT
0e (1)
where Q is the activation energy for creep at (Y = 0 an.[
i0 and y are constants. Under these conditions, the r.-,te of
Card 2/11

s/126/62/olVoo2/ol-Vo.,.~
Dc,)cii(~rn'lcc of .... E193/E383
crcc:, be corrclate~: -_,it7i the yield point of the alloy.
2) In crce:) cit Iii,,ji tei.i,)cratures and under low stresses the
diffuf,iou i.v~chanis;:: of dlastic defor!-.iation predominates and
there i- .,. definite toviperaturc ant: stres6 ranZc within -...,hich Cie
rate of ~;rec~) iricr(,a~.es linearly %.,,itiln incrr~asin,- stress.
5) in intemiediate ran,1;c of stress and temperature
defor.-:iatiun by slip ta'zcs place side-by-side with the rela.::,Ition
pro c er, ~; C.'3 The rate of creep can be obtained under
these conditions,from an equation due to J.J. Weertman (J. A,,;)l.
PhYs-, 1955, '26, 1213);
t = c(crP'/IZT)O'-")()Q/RT)
(2)
where a is tho activation energy for diffusion,
a' is the strc-,!-, and
U i coefficient e(:uallinL 5-4.
Th.c r_,LZe of tc,.i')erature and stress in which the diffusion
mechanis;:i of deformation predominates is wider in alloys t:ian
in pure ;.-ictals. The saiae applies to the range in which pl-istic
Card 3/1,

5/lz6/62/olVooz/cl2,/clU,
Dependerice of .... F.19~/E383
cleformnti,)ii in creep is described by Weertman's ecuation.
t:ic rtrc,.,:: dependence of tj;e activition energy for creep, cczi!;e~j
to be lii,.car at 6 - 71k:L/mil- for -mre nickel and at 10-1'-'
for t'ic' 60" co-Ni -1110y.
5) T:in o;wct of t:ic diffusion ;-nechani3m of -Anstic deforma'ioa
in the alloys studiec: is facilitated by polygonization.
There arc 12 fi~;urcs.
ASSOCIATION: Institut fizilci metallov AN SSSR
(Institute of Physics of Metals, AS USSR)
SUDNIT'I'ED; July 23, 1961 (initially)
March 2, 1962 (after revision)
card

NOSKOVA, N.I.; PAVLOV, V.A.
Defects of packing in solid solutions of nickel. Fiz.met.1
metalloved. 14 no.6t"-803 D 162. (MIRA 16:2)
1. Institut fiziki metallov AN SSA,
(Nickel alloys-Met 110 aphy)
(Crystal latticeB

L 16076-63 EWP(q)/kW(ix)/BDS AMC/ASD PAd JDIHWIJG
AcmsrcN iint Ap3Do46o$ 4/0126/63/016/OD1/0155~/0159
AUTBOIts Favlov, V. A.
717TEt I Hardenjrg of alloys by plastic deformation at torqyeratures producingi
anoxajv~e -relationsbip between Mecrianic-Ir-p-r-OP-5-Mes
SMRCE: Fikike metallov I metallovedeniye., v. 16, no. lo 1963p 155-158
710PIC TAGS: alloy,, hardening, plastic deformation, temperature, anomalous proper-
ty, , beryllium bronze, Fe-Vi-Cr-Ti. duralunin
AWMACT: Detailed experlmenta2 deta obtained in the study of the deformation
temperature effect on the strength and plasticity of alloys are presented in this
a f bigh-strength alloys were investigateds,17>e Y un bronze
article.4 Thr t r Ili
'r-1 'e~,,7e M-1
BrB2, F?'-I-. 114, and duralumin. It was determined that hnrUness 67 5r
increis-erwiTh The deformntion temperature and reaches a nwdmum at 350C, after
which it begins to decline. The deformption at optimm temperature produced a 3D%
ircrease in the elastic limit and a 25% increase In ultimate strength of the Lvtal.
The hardening coefficient of the Fe-Vi-Cr-A alloy reaches its maximom at 600CP
producing a 40%, increase in strength as compared to a sarple in Its Initial condi-
tion and one deformed at room temperature. In the case of durelumin, the rs:Kirum
Card 1/2

L 180`76-63
ACCESSM M AP~00/,,608
strength and plasticity vvere obtained with the preliminary deformRtion at 10OC; the
increase in strength reicbed 70%. The plastic properties of the earple so deformed
were =ch higher thpn those after the deformation at room terperature. Orig. art.
hass I table and 3 figures.
ASSOCIAMIZ: Tnstitut fiziki mvtiqllov AN SSSR (Institute of FkTaical retallurgy.,
AcederT of Sciences, SSSR)
SUBMITTED: l1Feb63 FY CL: 00
WE ACQ: Z?Aug63
SUB CODE: FL NO MT SOV: 003 OTMM: 000
Card 2/2

ti~&Fl oft L~z
L 17699-65 F,"eiT(m)/F.WP(-,d)/C4A(d)/,6VP(k)/ WP(t)/FVP(b) Pf-h/llad WWAID/W
ACCESSION -NR't W4042041 S/01261641017/006/0845/0852
Y -Petrova, S, N,t Pavlov,
vskly, V.-D,; Sokolkov a,
AUTHOR:: S adlo
V. Gaydukov, M. G.1 Noskova. No I . I _~~an_A__D - Y a
therm
al t
TITLEt The effects of-high-temoorature --o-me ch an i c
on the heat resist nce. of Kht 771YUR alloy
SOURCE': Fizika metal ov i metalloveetniye, v.-17, no* 61 19-64,
845-852
TOPIC TA(;S-.- nickel alloy,,, chromium containing alloy,, alumirium con-
p jrate, recrystallizationt boron containing alloy,
taining. a11oy,Sqjrje_e
KhN77TYuR alloy, thklmo_me~chanicaltreatmentv heat resistance
ABSTRACT: The method of hot plaFtic defbrmattoncombtned with quen-
ching w.as.used to enhance the stress-rupture strenathiSof ausitenitic
steelsq-- The authors investigWt_e~the possibility of applying this
comb ined -me-thod..-Za -KhN77TYuR.' V limonic-type alloy. Specimens
11, ~5 ~x~ 11e5 x: 70 mm were annealed at- IOSOC -_ for-8 hr, -and'rolled--
.with a reduction of 25% at a rolling speed of 1e5 m/min. The process
Card-1/3

L.17699-65
-ACCESSION NRs, AP4042041
of: -re crys ta Ili z at t od -was -suppre,ased, by water cooling -the- specimens
-immediately af ter pl.als tic de f orma tion. All specimens were agit d at
730C f (,r '16 hr. -Hardness was 285 118. At 550C and under a stress o f
2
_i90 kg/mm i, the rupture life was extended from 4 to 100 hr whilethe
creep r ate, decreased from 4-8 x 10-2% to,8 x 1071% per hr. Above the,
range a- deterioration of strength characteriatice-was 1. ob-
servedi, ''-The.authors attribute the.adverse effect of the combined me-
thod at 750t to~ the recrystallization during tes.ting and to a possible
her rate of coagulation of the at
g :rength--ening phase. The decrease
In'the creep rate and the increase of the rupture life were ver1fied
b x-iay-method. , The-authors int.out
po ... the. forma.tion of- a polygo-
_nizdd sub .structure :and to a, boundary distortion in.the form:of char--
.-acteristic. serration during high-temperature deformation. Thuy con-
the.
th substructural-boundarivs impeded the-travel of dialo-
catfonst-durfng~ creep, while the distortion of the grai'n boundaries
the susceptibility to-intererystallin-e failure.. The! authors
suggest. that the method of _inveotigation-may lbe. LnsufflcLently deve-
Ioped for an exhaustive 4hterpr etation.of the results obtained- and
of the peculiarities of the structural state of the material. Orig.
art. -has t 5 figures.
Card 2/3

("vera- c)vz5'y' ; FA*"L
(SvordlovnO
E Ir
cf an
preni~ltation LardenIng. AN S~~R. Met. no.r,tlg----

% 10260-66 M(m)/EWP(w)/T/EWP(t)/EWP(z)/EWP(b)/E*A(c) XJP(c) JDAW
ACC NR: AP5026369 SOURCE CODEt UR/0370/6!i/OOD/005/0187/0192
XOTHMs Gavdukov. M. Go (Sverdlovsk)j MalXshey. K. A. (Sverdlovsk)j Pavlov, V. A.
(Sverdlovsk)
ORGI: none
TITIJES Effect of chose transformation-induced strain hardening on the heit resis-
of iron-nicke'l alloy 1b
SDURCEs AN SSSR. Izvestlyas Metally, no. 5,, 1965, 187-102
TAGSt iron alloy, heat resistant alloy, nickel containing alloy, titans!
'containing alloy, strain hardening, iron base alloy, rupture strength, heat
resistance, iolid mechanical property
ABSTRACT.- Two iron-base alloys containing 1) 0.06% C and 28.9% NI, and 2) 0.04% C,
1*73% Crj 24e5% Ni, and 2.32% TI. were tested for,,the effect of transformation-
Induced strain hardening on mechanical properties at room and elevated tempera-
tuyes. Alloy specimens were austenitized at 12ODC and quenched In liquid
nitrogen and then annealed at 60D, 700, and 8DDC (alloy 1) are at 900 and 1100C
(alloy~2)-. In alloy 1 the maximum effeict was produced by annealing at 60D or
Card 1/2 UDC, 6 69ol5o24-177

t 10260-66
ACC Ws AP502630
700C, which Increased theyield strength'to 41 and 37 kg VM2, respectively.
Annealing at SW lowered the yield strength to 13 kq/vi~.41 and increased the
elongation to 40-46%, In stress-repture tests at 40M, alloy I annealed at 700C
had a rupture life of 837 or 55 br under a stress of 36 or 38 kg/mM2, respectively,
while conventionally treated (annealed at 1200C) alloy under a stress of 30 or 32
-k9/MM2 had a rupture life of 68.5 or 102 hr, respectively@ At 6ODC the positive
ef f e: c' t of' st'r,ain hardening Is maintained for a relatively short period of time,
knot exceeding 100 hr,. The effect of transformation-induced strain hardening on
alloy 2 was considerably greater. Alloy 2 annealed (after quenching) at 900^. had
a 10D hr rVpture strength at 7ODC of 17.5 kg/=2, compared to 3.5 k~/Om2 for
~alloy 1. Orig. art. has: 4 figures and 2 tables*
SUB CODE3 II/ SUBM DATEs 06May65/ ORIG REF% .016/ OTH REN. 002,1 MtrPRESSt
~i'60
Card 2/2 hw

IIOSKC,VA, N. 1. 1 ~ ; "' 1 V. A.
- . . :t,3 of packtnp, In fane-nontered -!ubJe, iratalti and allap.
- , /,. me". j m~laljoved~ 20 nr-,. "I zi,2&-4,32 A 165.
(MIRA l8il:)
2. instit-at ftzikl me-,,allciv 10 SSSR.

Ull TV KOV A? 11. F. ; NWWV A, N. I.; F AV LOV, V. ti.
Deformation &ifects of picking 'In rholium and irr~dhm,
Fiz, met.. I metAlloved. '0 S ~K
(MIRA 2.81
a. rnstituL fiz'ki rth~jt,3*llov Mi SqCIR.

41
7-1000-66 EWTW/rWA(dj/T/EWP( t__j/EWP(.%)/EWP(b) IJP(c) Mi-WIM
ACC NRs A - SOURCE CODE: UR/0126/65/020/005/0770/0774
'AWHOW Favlov, V A Filippov, Yu. I Frizen2.S. A.
ORG: Ing titute of Metal Physics L_#__kSSR (Institut fixtki metallov AN SSSR)
RIP
TITLE: Strengthening AV and V95 oluminum alloys.by thermomechanical treetv*nt
:SOURCE: Fialka metallov i metallovedenlye, v. 20, no. 5, 1965, 770-774
~TOPIC TAGS: aluminum, aluminum alloy, &OVA a4or-4
v9s,
Ilecha, nical A&** meW 01;-V
ABSTRACT: AV and V95 aluminum-alloy bare 12 am in diameter were solution annealed,
w& uanched,-.and then subjected to low temperature thermomechanical treatment
(L preheated to IOD-300C, rolled in one pass with a reduction of 20%, and water
:quenched. LITHT was-followed by aging at 150C, (AV alloy) or 120C (V95 alloy). LTTHT
with:: Irolling at'150C significantly improved the strenAth characteristics of " alloy
(see Fig* 1).-After LTrff and aging for 6 hrat 150C the alloy had a tensile strength
of 41.3 kg/in% a yield strength of 34 kg/m2, an R. hardness of 701, a work-hardening
factor of: 0. 7, and an elongation of 15Z, compared to. 32.5 kg/mm2, 26.0 kg/NM2, 70, 0.4,
and 22% for conventionally treated alloy* LTDff-also accelerated the decomposition of
..Card 1/2 UDC: 669.715:330743-

-1--:10890-66
.AICC NRj AP5028566
Fig. I. Deformation temperature de-
40
Pendence of tensile strength
yield strength (v0.2), elongation (6),
X and work-hardening factor (q) of AV
alloy aged at 150C.for 6 hy
v
X
the solid solution. Convbntionally treated alloy required 12 hr aging at ISOC while
t.hermomeIebanicafty.-treated-alloy required.only Chr. Alloy V95 exhibited similar be-
-havior bu*t was much less'responsive to LTTMT. After LTnff and aging at 120C for 6 hz
IV-95 had a tensile strength of 60.3 kg/mm'. a yield strength of 47.5 kg/am2, an %
-hardness of.83, a work-hardening factor of 1.0, and an elongation of 7.8% conpared to
37.6 kg/=29 42.2 kg/m2, $2, 0.92, and 91 for conventionally treated alloy. Orig.
art.. has; .7 figures and 2 tables. JDVI
SUB, CODE: 11, 13/ SUBM DATE: 293an65/- 6VIC REF: 003/ ATD PRESS-. $//70
Ld
2/2'

I ACC NR AP6WAl
-X-CA)-SWRCE CODE: uR/o4l3/66/ooo/ol2/oloq/oli
I
~WVENTOR.- Sinenko, X. P.; Mats, Z. Z.; Psyn, M. A.; Skazhennik, A. M.; Pavlorv, V. A.;
ubinfayn, L. Ye.
R I
tORG: None
I
PTLE: A unit for sealing turbine compressor bearings. Class 46, No. 182957 'Jan-
,,need by the Kharkov Transport Machine Building Plant im. V. A. Malyshev
l(Kharlkovskiy zavod transportnogo mashinostroyeniya))
I
;SOURCE: Izobreteniya, promyshlennyye obraztsy, tovarnyye znak-i, no. 12, 1966, log
PIC TAGS: sealing device, turbine compressor, journal bearing
OTRACT: This Author's Certificate introduce& a unit for sealing turbine compressor
!arings used in diesel engine blover systems. This unit contains labyrinth packings
.th air seals fed by compressed air from the turbine compressor shell. Oil is kept
it of the turbine compressor during idling and lorw-load operation by connecting the
x seals to the locomotive braking system vhich is coupled by an electromagnetic
Llve interlocked vitb the locomotive control system.
1/2
UDC; 621.515.5-762;62;621.436,052

packingsS 2--air seals; 3--compressor shell; 4 lectromagnetic valve
CODEt 13/ SUM DATE: 12jun65