SCIENTIFIC ABSTRACT PINES, B. YA. - PINES, B. YA.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001340920003-9
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: June 15, 2000
• Sequence Number: 3
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

i,9430
S/Iiq/60/000/01/ooll/olil
Eq%j--ji
The Problem of the Role or Clo5o-d Porc, I n t fr i n r i n P(,,- J , r
Metallurgy
formation Under tlie microsr-ope it L-, totind tliat Al
particles tend to di-sappoar wilile tllc. (initialtv) Ni
part6cles expand (Figure 8 for `!,O~. Al mi-\tliro 8 110111 ~ 11
620 C, then heated to 1 -'50 oC aild lmlllediatolv fooled.
X 400). Finally. Figure 9 show,, ettrinkagto a-i oa f titic t icort
of composition for I . -j and 5 hotirs at 1 -'50 fullowititz
heating for 8 hours at 6.!0 OC. Tlivr,- i- a glight expan5ion
for mixtures - 15 - 451. Al It is rmpha~iirefi that III
sintering a mixture of nater ial- . it IN Irlillort"Irit Ito ollt~z,lom-
at temperaturpq below the. molt trig point of anv C or] 14 t I Ili ell I
There are 9 figures and ~ Soviet I of et owL #.-;
ASSOCIATION: Khar'kovskiy guquniversit et imeni. A.M. Gor krlqc~
(Khar~kov Stat e Uri)vei sit v imeni A.M. Goi kiv I
SUBMITTED: March 11 1959
Cajw V 4

/.P Y 2,
/P f .200
AUTHOPS P=es, B Ya., S.IrAnko, A F
TIl"a Dif Pus ton ' --ap w~d k1-)n-Fq,_1 F~-
:ae*~ M-~*,Als
PERIOD11CAL, 'Iz-vestlyp vvr-zf-.1_kh ~-_nebr~ykh zq---J-Y,
1960, Nr 2, u, P1 - 89
TM ne f;-Ilow:-,,g Je 1!it'.3n4 from
,)bserved during invs~Rtlga,~ Ions ln*r~ dlff4~1-,n :--iop rsf fr-i%al
presence of an -ansettlad -reap 51-ag-, jl-
an the magnitude of appilAd str-:-?s, a~.a and lof
tension and covppress!,!.n, ant r-d-jcsd values -f *.t-- P,
-reev, I.e., Ir.'- ~ * , " q.*,-:-
-,, , a'
ceramics subJe~~*.Ad !c -r-ssj-Q w-r- -arried -.J*
-,~opver wIth-e- 50,j~ grilt sl?a unde, a _,,aJ :0 nmr 's A hljzr.-
va!=m do~vt ce, shown In Figura .. was uc4 -mvr4 q.--'
Results of exporimarts ar,~ g1vAn In Tat' ~ WaS -~5*-At._'Shad *hil
obsArvad w.,r,? .-3u4-d 1-v *.r,A r-n
Ca-rd '/ 3

S1 148/60/000/W~/00 t IVO
Diffusion Creep and Non-Equillbrium State In Metal Ceramics mnd - M-'
They --an be fully eliminated by sufficiently extended high-temperature
annealing. Furthermore. Investigations were carried out Into crtlei af*-r
hard facIng of metal ceramics pressed from Iron powder. fleaults :f ex-
periments are given in Table 2. It was established that hard facing speeded-
up diffusion creep at high temperatures (e.g. in Iron at 9DOOC) mainly at tha
unsettled stage. At lower temperatures (7000C for Iron) hard farl_ng causqd a
decrease In the creep jate. This proves that creep at such temperatures has
not a purely diffusionlrbut probably a dislocation nature, Results obtained
from experiments with Co-NI, N1-Pe and NI-W powders [Ref 6, wor,- ana.log-us
to those obfained with other systems including the Cr + Mo systems. P'.1re
component afid 50% Cr + Mo powder imixtures were tested at 1.3000' in a vacuum
under a load of 75 g/mm2. The samples were preliminary anncra:el In a v-A-IUM
at 1,3000C and 1,5000C for up to 14 hours. Aes deformation -re-p.
shrinkage in sintering during preliminary at. Aing was studial. Pnsk;l*~s
experiments are given in Figure 4. It was established that -renv
was always accelerated (mainly at the unsettled stage) in I-,-,ving
excessive vacancies, axising as a result of non-uniform partlai hA*-,
diffusion. In metal ceramic samples of Cr and Mo powder mixtures, *~P --v
Card 2/3 .1 1

S/ I 48/6(J/CX,/Vi 21',,(.) 11:,/'j ~ I
Diffusion Creep and Non-Equilibrium 3tate In Metal CeramicS vid Cnsl Melt
acceleration was correspondingly low at 1,300c)C, when haterodiff'UsIon o~
Annealing at 1,5000C during 50 minutes delayed the creep of pura componont
samplesi on the other hand, the creep of powder mIxtures was a,,aloratad
After exCended annealing (8 hours) creep of powdAr mixtura5 win Aii?wr-d 'i'~WTI du,
to the gradual elimination of excessive vacancies
T'here are: I photograph, 1 diagram. 3 tables, 3 graphs and 6 3?vlet
A3SOCIATIONi Khar'kovskly gosudarstvpnnyy unlverslt-r (Kha.-'k.~.- 3-1-
SUBMIWEDI March 19, 1959
L41
Card 3/3

3/148/6O/OC)O/W5/CK~5/1J_ 9
AUTHOR.9i Pines, B.Ya., Sirenko, A.F.
PV
TIMLE: ffRecove-y" Under Loa ease3 of Difflislon Creep of Me~.-k_
Cerami~,s
FUIODIZAL: Irvefftlya vysshIkh uchebnykh zaved-inly. -hernay& motailurglya
1960, Nr 5, PP 121 - 129
TM DlMslon~ i:.reep In porous meta_' cera;rl,~siwa4 studied by i-x-
Deriments made with specimens pre ed from copper powder'Kelectrolytt- orIg1r,
grain size -~- 50A-), nickel powder1reduced from carbonyl; grain size 1u - 15~
and tungste .~grnln size 5 - 10,A-) The experiments are Illustrated by a
numbqr of graphs. it was established that metal, alloy and. particularly,
metal ceramii~: specimens, subje2ted to diffusion creer at raised temperatures,
r.-.vsa_!ed consIderatle retardation of other diffusion processes, such as sin-
,.ertng, recrystailltatlon and heterodifflusion. This retardation was connected
with the non-equilibrium state of tile specimens and arose In connec-tlon w1th
the grad4al approach to the equilibrium. Diffusion ~-oefflclents decreaso-d
corre3pandingly. Thus, speeded-up "recovery" )f equillibrIun. propprtlps under
1/2 A

S/l 48/6o/ooo/oo5/0r,5/JU9
"Reoovery" Under Load in Processea of DIffunion Creep of MetAl Cernmica
load occurred.- Retardation of diffusion processes at various temperatures
was propor-tlona-1 to the rate of diffusion creep, if applied strain was
constant. If at various temperatures "corresponding" strains were applied,
which caused the equal rate of creep, the retardation of diffusion processes
was the same. The retardation of diffusion processes in diffusion creep did
not depend on the sign of the strain applied, and was equal during tension and
compression. The first non-steady stage of diffuGlon creep may be interpreted
as corresponding to the decreasing rate of creep proper, resulting from the
speeded-up recovery of the regularity of the crystalkInk- lattice and the
equivalent values Df self-diffusion constants under load.
There are; 10 graphs, I set of micro-photometric curves and 6 Soviet. references.
ASSOCIATION: Khar'kovskiy gosudarstvennyy univers1tet (Khar'kov State University,,
3UBM!7.TEDs March 19, 1959
Card 2/2

AUTPORS:
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S/126/60/009/03/010/033
E091/E435
AUTHORSt Pines, B.Ya. and Chaykovskly E.F.
TITLEi -&fltience of Plastic Deformation of Nickel on the
Diffusion Rate in the Ni-S System
PERIODICALt Fizika metallov i metallovedonlye 1960, Vol 9, Nr 1,
Pp 369-373 (USSR)
ABSTRACTi Specimens of the shape of rectangular blocks,
5 x 5 x 10 mm, were made from technically pure nickel.
In order to remove distortions due to mechanical working,
the specimens were annealed in a reducing atmosphere of
hydrogen at 1000*C for one hour They were then detormed
in compression and the degree of deformation 6 was
determined from the formula
1i - 11
6 H . 100%
where H is the initial thl--kness of tile specimen and
h to the final thickness after compression. The
maximum degree of deformntion wam 80%. After deformnt loti,
the specimens were subjected to diffusion Annealing lit
Card 1/5 sulphur vapours. Several specimens with various de.zrees

S/126/60/009/03/010/031
E091/E435
Influence of Plastic Deformation of Nickel on the Diffusion Rnit, in
the Ni-S System
of deformation were annealed simultaneously. In order
to determine the diff'usion rate of sulphur in nickel
the thickness of the layer of Ni-S compounds formed
during isothermal annealing was measured by means of a
MrM-6 metallurgical microscope or with a micrometer
Two methods of Annealing were tried, the first as
outlined by Presnyakov I a paper (Ref 6) and the other by
annealing nickel in sulphur vapours The first method
proved to be unreliable The second method. which was
adopted by the authors, involved annealing in a special
aimple vacuum apparatus in which the vapour pressure of
S could be fnirly Accutately attained and controlled
independently of the diffusion annealing temperature of
the specimen. The appnratus has two nichrome heater--4
mounted on one vertical porcelain tube, The lower
heater volatilizes the S and the upper one is a
furnace for diffusion annealing in the middle portion of
which the nikel specimens w,~re placed on a holder.
Card 2/9, Above the second heater is a (-o,)Ier on which the S

S/126/60/009/03/010/031
E091/E435
Influence of liastic Deformation of Nickel on the b1fluinion Hate
in the Ni-S System
vapours condense. After each annealing, the S
wag scraped off tile walls of tile cooler and thrown
into the lower volat I It z i ng f'ur-lljjC(b. Th P qua n t 3 t y , I
S in the volatilizer was chosen so that this el---)Pnt
should not be able to volatilize completely during tne
maximum annealing time. The upper portion of tile
porcelain tube,through which the ends of the thermocouple
were led to a hermetic seal, weire connected to the tube
for evacuation and pressure control in the apparatus
Evacuation by means of a vacuum pump reduced the pressure
in the apparatus abovt- the cooler during annealing to
approximately 10 2 mm Hg . The temperature (if the
volatilizing furnact. was maintained at 3UO'C whiftl
ensured a S vapour pressure in the working space of
the furnace of approx 50 mm fig (Ref 7): tile temperatures
of the volatilizing f'urnace and the diffusion annealing
furnace were controlled by two nickel--nichrome
thermocouples. The lay-out of the apparatus is shown
Card 3/5 in Fig 1. Diffusion annealing was carried out at 4'1(,, C

S/126/60/009/03/010/033
E091/E435
Influence of Plastic Deformation of Nickel on the Diffusion Rate
in the Ni-S System
for one hour, at 500% for one hour and at 6oooc for
15 and 30 minutes. Control runs were carried out at an
annealing temperature of 700*C. The results are shown
in Fig 2. The dependence of the thickness of the Ni-S
compound layer on the degree of deformation 8, which
can be found experimentally, enables the change of the
diffusion coefficients D of S through this layer
with increase in 6 to be determined. For the
evaluation of D, Pines, ratto 0 a e2/4t was used
(Ref 5). where t = thickness of the phase layer forming
as the result of' uniform diffusion, t = time of'
isothermal annealing. In Fig 3, the values of diffusion
coefficients thus found in relation to degree of
preliminary deformation are shown for Ni specimens
annealed in S vapours at 600% for 30 minutes. From
the values of D found, the activation energy of
diffusion of S vapours through the layer of nickel
sulphides formed were determined from the relattonsh~
Card 4/5 log ID There are 3 figures and 9 references, V)
T

80085
Ir" 6joc 5/02~60/13i/~6
A uT duas Pines B B014 B007
j 11 - Ya. ,_6irenko, A F.
:.r,: rit, Problem Con...,,n,.. the Conditions
str-ctlOn Processes Of Xetals Jnder 01' Avversibility of thc- L.
11RIUDICAL: DckladY Akademil naux Vol. 15 1 , No. 6, pp
Tz:,X7: The - Y pori merits described WIL~r(? made with powder-notallurgical samples
which were :,rcosed from electrolytic copper. The samples had an initial per-,t
of 17 - lbA, which was reduced to 5 - 4): by sirterine at 10500C (for 24 hour-,,
The life of -i series or 35 equal aamples was determined after applying the s-,7L'
load in each. case. From these vallues the average life was determined, The 11:
of a further series of 35 sam.les nder load was deterinined after intermedia-
anncaling. Also in this cane the average life was deter,ninvd. In Fig- 1 th,, ~ -
sults of llft~ determination at ro~Lj temperature without ~ntermsdiate annegli;.,,
and or life in the case of intermediate annealing at 600 , 900 , and 1040 C ar-
Rraphicallj represented. In Fig. 2 the analogous results of durability determ;-~i
tion under stress gt 6000C are shown- It is found that internediate annealinf,
four hours at 1040 C produces the same results as intermediate annealing for
Card 112
80085
of ReversibilitY S/0'0/60/131/o6,~25/071
Conditions B014/BO07
The Problem Concerning the is Under Load
of tile Destruction Processes Of Meta
0 for a complete h"ling of defects, annealing for 35 hours It
hourl; at goo C; 3 graphically represents the dependence of the quantity
10404C is necessary. Fig, me t ('11 and g 2 are the life before and after inter-
A.1 a i - - i on the ti
1 "2
mediate annealing, j is the mean life without intermediate annealing). Herefrom,
cter of healing. By extrapolation
conclusions are drawn as to the diffusion-chara. ling time
of the straight lines obtained from the experimental data, the annea
necessary for complete heeling of ths defects is determined as being 105 hours at
6000C, and as being 16 hours at 1040'C. The ratio between these two times is
about 7.2 and corresponds to the ratio between the coefficients of the self-
diffusion of copper at these two temperatures. Thus, all arguments indicating the
diffusion-character of the growth of cracks after stresses are strengthened. There
are 3 figures and 5 referenc*s, 4 of which are Soviet.
ASSOCIATIONs Kharlkovskiy gosuderstvennyy universitet im. A. 14. Gor1kogo
(Kharlkov State University imeni A. M. Gorlkiy)
PRESENTEDi January 15, 1960, by G. V. Kurdyumov, Academician
SUBMITTEDi December 12, 1959
Card 2/2

ACC NR, j ~ J9 SO~;'- CE CO. 2! 06 3 5
A P7, u
AUTHOR: Pincs , i). Ya. Kar-nazin , A. A.
ORG: Khar'kov State University (Khar'kovskiy gosunivemitet)
TITLE: Concerning the activation eiorgy of the terri,erature bacxground of inter-T,al
f-rict ion
SOURCE: Fizika Metallov i metallovedeniye, v. 22, no. 4, 196b, 632-635
TOPIC TAGS: activation energy, internal friction, temperature dependence, crystal
dislocation, impurity level
ABSTRACT: Two standard equations were given for temperature dependent internal :~ric-
tion: A exp '41 %:' t-- 1, kri.
T
In these equations it was no-ted that the ac-,iva-ion energy of backTround i.-.-Qrra~
friction (U) was very different from the activation energy of the i-rain p~-a~<
(VI). For example, in Cu the value of U, is 48 ~-.cal/mol, w.-.ile U is only 8-1~ kca-*/
/mol. No internal friction mechanism could be related easily to such low values of U.
Therefore a new equation was presented: K fu) exp (&,!k7)1-".
UDC: 539.67

ACC NR. AP7005139
where K and n are constants in a particular temperature range, U0 is tne actlv-'
energy for viscous dislocation flow, and w is the oscillat"on frequency. -,%e value
of n could be obtained from the frequency dependence of Q_i, and was related to L~ ty
U = nUo. Values of U, n, Uo, and activation energies for self diffusion were tabu-
lated for ten different pure metals, in various temperature and frequency ranFes. :n
every case, Uo was equivalent to the activation energy of self diffusion. Valuei. of
n ranged fron 0.17 to 0.38. The experiments quoted were done on vacuu;n penC'a.-,;-,s of
the Ke type at frequencies ranging from 0.25 to 3.3 cps and &-nplitudes below 2-10
Data were also given on the effects of linear and point defects in pure aIuni-.,,,,z-,. Zis-
location densities were varied by cold working different amounts ano Fe, Si, ar,5. Cu
additions were made up to 0.3%. Values of U ranged from 4.0 to 11.0 kcal/mol; how-
ever, U0 did not vary by mom than 10% from the 99.9998% aluminum value of 36 kcal/
1 wa re ate' o
/mol. From a phenomenological point of view the new equation for Q S 1 ~ t
a broad spectrum of relaxation times T -to exp(Uo/kT), where Uo is constant; triat is
A~ WT - dj.
call,
where dz is the n=ber of values Of To in the interval dia. Orig. art. has: 2 tables,
6 formulas.
SUB CODE: 11,20/ SUBM DATE: 1BJan66/ 0.~(7G RLF: 1-03/ OTH REF: 062
-C.,u 2/2

ACC N;:
AUT1101i:
WIG: K'~).,.
T IT 11. 1
P14, 7. 1
-roil 1 '71
i XA jai r I 111 rk, I,k,
C r :,A 1. ',k) ~Ll I--)1 r i ~)V. II& I., J)I-W, ;t;0:-
clasucit). -.:it. authors 014. f (h !,0iU!,1c Illytlrltj~- -r!
tell J)c ratUrk !Cj- 1) wi t resjwc i w u f 01c C u - N I s
0
series of soilu buiutions (cu - 5. 19, 1:1, 30, -iU, and !)Ot Ni). pu a.,-
Card 1/2 L:DC: 66J. 3: 539. 5

ACC NR: A! 17tj 0 ~-" , G3
ius E of ciab--c;t), increase wAli increase in the N. concentration oi d~c aliov.
-1
1. 0. t.,L-
0 - i-i of linear increase in creep) 'Incarly decreases with n,-rc-t:.
and rcacne.,, %%,.,~n - T M. P. Neverlhelc.,-~s, 1)0:annot be regarded as ,in
point aj high at which uilfusjw~ c r, cp occurs, 5ecause the valu( o'
-worked n,i aliovs are lower than in specii.ens a;.rwaled at high ten.i,cra---t
X mediur-tv.:,- crutures prelirnin:Lry co)d wurx.m, -awses !iardening of tne metal
dation of crucp rate, whereab at tcmper.,,turc,,, cl(,.~e to the melting point prvhrr.,.:~
Mirking to ",oftening" of au metai ai,,i :se in creep rate. There is .11 -%("
fur this phenomenon. I., C. DL 'i8.SL)C1atVd Md-I k:.
equilibriunii) concentration of vacancies uccul-;-.;ii, -,. Lhc I,resence of a large nun.tj~-
locations wh.,ch r,,sults in an accelerated climb of ;isloi --.ions. " The authors are
S. S. Avotin for participation in preparing speci-mcis oL, the alloys." Orig. art. has:
SUB CODE: -6/ SUBM DATE: 311May-66/ )!~IG REF: 00o/ OT11' REF: Ou',
Card 2/2

ACCESSION NRI AR4018311 8/0137/64,/ODO/001/0036/0035
SOURCEI RZh. Matallurgiya, Abe. 10248
&U711OR i Pinoc, B. Y&.
TITLSt So" aspeota of tho thoory of aintoring of mfttnl powders
Cl MM SOURCEt Tr. Kuyby*9hr)vnk. -tvinta. in-t, ryop. If;, 1963, 111-133
TOPIC TAI;')i m-,tril po-~il-r (vinterinr,, povrilnr ninterinf, thnory
~ANSLAT : IN t wi t It 1 1 -, p - -),i ri 3 1 ri s t n * o r i nj- I n 7o I i pripp I u -i i -n A r ;i, r
t~ln i nif I tin n,- A of' i I I - r, r - n i . F rN r i'd n I th,w 7- , wh i h ti I
tll 71 q r -) jr, ,~x n it t-r i~i r t ~i- I n! I i- n - It ry
t~ I r V
~l if- 11, -1,1! r 1 111 It, I"
'r.,
I r 'I h
U ie ory of' Mid it- 11 t_ n 11 r Ii , IT It
fo roo o . 1u the oix3o if filuL~rlrig, tho j,!-)n)q:a 19
stato of tho cryatal IRttiac mmil the ohnrAnt,~r of ita dnrecta 1
Card 1/2

ACCESSION N`Rt AR4018311
in the ocyurse of aintering. Disloostionn and vacanoise have different offoots on
the magnitude of the difruaion oooffioient. 0. Padalko
SUB COM W4 KNCLi 00
Card 2/2

P11M. 1. 1. , Prof.
,
OThernpeutic lise of amino acids in neuropsychic disenses' b.V A.L.
Andreev. Reviewed by A.I. Pines. Sov. med. 22 no.12:116 D 158. (KIRA 12:1)
(AMD10 ACIDS) (IMRVMS SYSTM-M-DISUSMS)
(Ah-DRM, A.L.)

~_iL~ 42117-6~ EWT(1)/FWT(M EPF( EWP b)0 Pao-2/Pa-4 LJP(c)
I(Zbj
ACoCE35LON NR: APS001656- 79 5'1000/0011019Z/0194
AUTHOW jpInev, B. Yai; Ko~ile'nko. S.L
TITLE: - Multifrarne high-temperature electron-difir ction camera
SOUItCE.-, -Pribor'y I- tekhnika eksp
arimenta, no. 1, 1965, 192-194
GS. -electron diffraction camera
C~;,TA
-A-BST CT*. -.--A- n- a --- *-p~oitool4tir magazine capable. of-producing _24_picture,~ -.bn lour
*Ithdut -reloading to-described---Mle new elect
91CIZ-cm-platex ron-alffraction
-ecirnen
camera is equipped three' sp holders (independent specimen heating)
ch can be succeosijely introduced into the electron beam.
The opecirdells are
ste'ned. to tantalum
hirips which carry the controllable heating current. Also.,
tranxillum.1,11nat-lan of film-type specimens is provided for. Sket ches of the camcrA;
'and specimen holder are supplied. Orig.. art, has:, 3 figures.
z'~"f~ASWdtATION:.'IChailkovskiy univ, IaLr-sitat (-Khartko Y University)
SUBWTTED1 ZSDec63 ENCL: 00. BUD CODE:
.1jQ REF40Y.- 003 OTHER9 002

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..3h896-65
Jet AP3MW~
vulis annealiql (in a furnace vvt-u- fifilar beating coil)
:",-a 0 as on A
avit exposea- to. cosl&* - I- to 5 1j/M2j, In a cycle donsisting of rapid
besting., soaking tow three houra without load,.soaking for five hours under 2*ad.,,
-andrapid C to row teqperature-. :The annealingAesqWatures, were 300., 400.t
and 45W
lberemdta show that different vorking temperatures correspond. to dif
fereatdogrees of unia3dil magnetic texture* The'experiments' have shown that
following the theramechanical vorking the dependence of Ahe niagnetortriction on
~the mapetic field'is nomonotonic. Noregular connection1could be established
~tbe'
additional vob=e striation and the load. Measurement of the elastic
-between
constants. of thi ferrite after the therimechanical. treatment exhibited some dif-'
M:
ferences -between ferriton subjected totherumechanical ad to thermomagnetic
treatmentp- and it Is, concluded that the detqLU*d machanion of establishment of
the wgustically uniazial texture is different' In the two prooseaest althaagh the
ad result.(residaal. deformation of the crystallattice) is the san-t- in baLb
0"418 6- Orig.__ arto - bas t2 ~ figures..
F'-AOSOC=Ovt _DMIkovskly gosadais _W1ivvr#ft6t.(Mw'kvv Statt University)
BUIR412M 2, Mkpr6k 0 zi 00 WD CM1 Saj IN
I P
10 MW sat 00 001
P
2

W WIEWT(M)IDDS AFFTO/ASD JD
AbbMMAAs 03000201 3/0126/63/015/004/05%/0591
-2. Ya. Sir*W-w A.F
NS,
U
Speed,of the diffusive creel
in mstal~at submelting temperatures
1. 3DUSCU Mike owtanow-1, astallovedenlye, vol. 15 no. -4. 1963* 584-591
"PIC TA93s creep in metal', creep in copper, velocity of creep
ABM7tkCTt According to the existing postulates, the diffusive creep in the homo-
;Sensously stressed bodies in caused by,the oxistence of atomic sources and voids
inside
abd at the WiPhOZY of-the body, the4ormlas expressing the speed of &
Study
diftwivi creep derived by C. J. 1 Herring,. i, - Ms, Lifshitp
# J ~ Harper,,
L ShepajdL -'and J.' Min are Compared; the theoretical and ;;peilmental data'
Conce.rnivg the affect of the specimen substructure on the creep velocity are
"discussed..,The experiment involved the et
(under tension) in 23 electrolytic a *dy- of Lhe creep velocity variation
19gMr),Aamples, The, sanples,, .4-iffering in
'grain slsas,, were sutleated to yaj~jcua treatments before experiment, The creep
j
'"Iftity asaxaraw X in all the samples were made at the. same t rature (1040C)
Ova
i and UsA (p-2 The experimental conditions corresponded to the diffusive
1/2

I 186~2-63
ACCESSiOr 'AP& 101
Vreop the v81" Ity d. which doond a *a the opplied stress p. The creep plocity j
it bOOriid in thM~specimens was in the interval from 5.6 x 10--' l/sec
tiopo
difference In the'speed of a
t 210"OL: I/sMQ' -~ the authors conclude that the
I at the temperature W400 nay amount to more than 3 orders of magni-
*SOL Creep
j structural state of the
L 0 and that *sod varies on. the structural and sub
U
determinod' by the kind of the preliminaryL treatment. However,, neither
ep n
Crilreass-owmed'-sabstructure types, which deterwIne the distance between the atomic
o=va mid Voids ianlexplain the broad range of 4*locitj-v&riationa. Possib.3,v
ithi*: a Mats obtained experimentally were caused by the superposition of various
luctura* types* "Orig, &et.. has: 4 formlas,, I tablep arA 6 figures.
raitet in& A, K. Gorokozo
AS04MIONs' Kbartkovskly gosud&rstv9nrgr*y unive
"I (Kba-0kov $tat* University)
TOM =8 UTY. Ar.Qs 362Jun63
SL 03-UPW ENCLs 00
$U9 MX1 ML NO RV SOVI 007 OTHM 002

PM/01) JD
.1"23h19-63
0/032/63/029/003/011/022
AVZRMS. Pines. D. Ye. end xvaa~V]1-1!
TITLE: Preparing monocrystals of Up Cu. end Cu-NI. alloys In a vacuum
smelting furnace 4,
4,1
-:MXODICAL: Zavodskays, laboratorlya, ve 29,, no. 5,, 1963 5%- 5"
TMCT: A "a Imple method of forming monocrystals of dIfficultly-fusible
met~Bls, nickel, copper and nickel-copper alloys directly from fusions has been
vorked out. The molten alloy,, In a crucible,, to driven up into a airconi=
test tube by nitrogen at a pressure of I atmosphere. The temperature is lowered
to several degrees below the solidification point of the alloy and kept there
under vacuum for 1 hour. Then It is slowly cooled.5 Monocrystal6 up to 100
in length MA 3-5 am In diam. have been obtained. There are 2 f Igures.
'ASSOCIATION: lharlkovskly gosudarstvennyy universitet In. A. M. Gor1kogo
(MK'koy State UAIMrsIM Imeni A. M. Qor9kI
Card 1/1

PIM , B.Ya.; SIRYNKO, A.F.
Regularities of the creep kinetics of metals at high temperatureB.
Fiz.tver.tela 4 no.10:2727-2732 0 162. (VJRA 15:12)
1. Khar'Wvskiy gosudarstvennyy universitet imeni A.M.Gorlkogo.
(Creep of metals)

PINES, B.Ya.; SIRENKO, A.F.
Mechanical properties at high temperatures in equilibrium and
nonequilibrium states. Fiz.met.1 metalloved. 14 no.5s693-700
N 162. (KIU 15:12)
1. Kharlkovskiy gosudarstvennyy universitet im. A.M.Gorlkogo.
(YAtaU at high temperatures)
(Phase rule and equilibrium)

L 1~~- ?t
17, If
5/070/63/008/001/003/C24
E132/E46o
k U I 11o1? 5 f1i nes, li.ya., Grobtlyini1j, 1.11.
TIFLL: Electron diffraction investigation of heterodiffusion
in the system Go-Si
FLRICDI~ k1 : f\t l"Ota) lillgrell'IYA. v.8, no.1 , 1963. 16-20
TE~:T - An est ima t e fia s been inade of t lie coof f ic i ~nt of hot Pro-
di f f %is t on be tween very thin layers of Ge and Si at 840"C . This is
not significni-itly different from the value found by D.A.Petrov,
YU.t,.3haqhk,)v. tind T.P.Akimchenko (Collection: Voprosy metallurgii
i ftziki polviprovodnikov (Problems of Metallurgy and Physics of
Semicondxict,rs) izd-vo AN SSSii, 1957, 130-132) for massive
specill'ons. It is often aq.,5erted that the diffusion coefficients
when Invers of only 100 to 1000 atoms thickness are involved
differ from the bulk vnluen. The length of time required to
erpinlize the concentration of Ge and Si throughout n thin layer
Sives a mva.--ure of the difftision coefficient. This process could
be followed by electron diffraction as a double layer was annealed
in the camera itself. Go was deposited on a substrate at 400*C
alit] N layer of Si was evaporated on top at room temperature. The
Go layer was crystalline and gave sharp npots and the Si layer was
Cnrd 1/2

S/070/63/008/001/003/024
Electron liffraction ... E132/E46o
amorphous At 1150-5000C the procens of equalization of the
co"ce"tration had riot yet begun. At 800% the Si crystallized
and at 8400C the system became single-phased. From the time
required for this process and the thickness of the film, the
diffusion coefficient could be estimated as 3 x IXY-i4 cm2/sec from 4-
the equation X2 . Dt, where x is the thickness and t the timej v
t was about 120 mec at 840*C and became too short to measure at
higher temperatures; x was about lo-6 cm. The. are3 figures.
AS-OCIATION: KharIkovskiy gosudarstvennyy universitet
im. A.M.Gorlkogo (Khar'kov State Un*weraity imeni.
A.M.Gorlkiy)
SUBMITTLD: June 16, 1962
Cnrd 2/2

S/18 62/004/010/012/063
B 108YS 104
AUTHORSi Pines, B. is., and Sirenko, A. F.
TITLEt The kinetics of the creep of metals of high temperatureo
PERIODICALi Fisiks tverdogo tela, v. 4, no. 10, 1962, 2727 - 2752
TEXTi The laws governing the creep of metals were studied on specimena of
electrolytic copper, previously rolled and annealed for 20 hro at 1C1,00C.
The change in load necessary to maintain a constant creep rate over a wide
temperature range was checked in order to verify the formula
V . ALPnsIP(-,jRT)
(J. Dorn. J. of Mechanics and Physica of Solids, 3, 85, 1954), where V is
the creep rate, p is the load, , is the activation energy. The experimen-
tal results obtained with an arrangement described in FUM, 7, 766, 1959
showed this formula to be correct. The exponent a decreases mith increas-
ing temperature down to n - I at about 9500C. There are 5 figures.
ASSOCIATIONs KharIkovskiy gosudaretyennyy univerattet im. A. M. GorIkogo
Card 112 (Kharlkoy State University imeni A, X. Gorlkiy)

The kinetics of the ...
S UB)l ITTED iM&Y 7, 1962
S/18 62/004/010/012/063
B108Y8104
1
Card 212

S/181/62/004/012/008,/052
B104/B102
AUTTIORS: Pines, B. Ya., Kuznetsova, R. I., and Dubovik, M. F.
TITLE: Development of submicroporosity in composite electr)!Ytic
films of the Cu - Ni system during heating and load,~np
P'_'RIODICAL: Fizika tverdogo tela, v. 4, no. 12, 1962~ 5409-W4
TEXT: "he scattering of X-rays at amall angles and the kinetics of the
destruC tion of thin electrolytic films of pure metals (Cu, Ni, Fe) were
investigated in continuation of previous studies (B. Ya. Pines, R. :.
Kuznetnova, FTT, 5, 1475, 1951; 4, no. 5, 1962). The change of a-it -
Microporosity in Cu-Ni films iurinC annealing at different temperi-ares
without and with load (250 el=2~ was studied by means of X-ray scattering.
A copper film was electrolyticaliy deposited on a polished steel plate,
then separated from the plate, annealed and electrolytically coated on
both sides with nickel. The total thickness of specimen 1 (17,1) *as
composed of 85~ Cu film and 15~6 Ni films, and that of specimen 2 of 50~
Cu film. Results: a maximum volume of pores was found in the films,
exceeding that of single component films by one order of magnitude. This
Card 112

ve I,,;, men tq , t,r, ic r,iporon i t.,-
04 B10,'
e x r. e 3 b y al J - t Jnii '.fr z-tr. tares thro,ig.,. noro;nf,:*~: T it
hetero,i,,ffusi:)n ~Frenkel' effect Df firf-,t kind). Under anne;ilinr, at lill-'J
subn~.Croporosity in the unloalel s t it t e i n r re a a e a a It If 1 r s t , p a s!3 e ; t :. -,,) ~ (,,,,
a maximun arA then lrkv~;. '~ nn e % Iini- in,ler load always lents t ~ ;,n
in nubinirroporo2ity; the hirher the annealing temperature, ti-,(?
the increase. The levelopment of submicroporosity in conseq,ience -,f
heterodiffusion leals to a noticeable reduction of the hea,
offered by the composite Cu-Ni films. The amount of this reducti-r. is
determined not on:y by the total vol-,ime of the pores but also uY tneir
dintribution in the film. "here are ~ figures and 1 table.
ASSOCIATION: Kharlkovskiy iosudaretvennyy universitet im. A.M. Gar'koF-,
(Kharlkov State University imeni A. M. Gorlkiy)
SUBM IT TED July 2, 1962
Card 212

4 irl;,ornt iii rivch,mi c al :ji r i
ec I 'T1 (,I I I Ti 11 o 1.111 1 1 1 1) r I um , I it f I I I f I -
r i itI II , r Ii ir n c r id It i )n
P FM 101) IC Al. 1 7 11% a 171 '-t I I ) I I V k III I I, od on I N' V , V I , Ili)
69 1)
'I I'XT - e ra t e t f FIT -s 1 r, n it roc es 9 es . whi I c )1 1) a N- In impor t ant
part in the deformat ion (if metal., at elevated teniperaturos, (Ipi~ends
on whether or not the met.)l I, in I ntate of equilibrium. Th i ; c in
lie explained in t orms of I hvpothf,91% that the proces, of ''hi-al Illu''
o f d P f ec t q I TI a d I , ( " r t c r y ~ ( a I I at t Ic e 1 % acc ompon I l"l I " t it .
formation w it ( on,i,I~~, nulliller c%( v\cc%R'~ vacanclp~ nri '~I .I It I ti t'
a the d i f I u qi o n ;) r (t c o e 110 ,it I '-( 1, (1 1 t 11 0 1.1. V -A Ptit IIli, ,,, I t -
I')lj IL . c I I v( I t it I I A I \ ~1 I t tA I I I \.' r"I t I I v s 1 .1 11 \ '' 1, t 1 1 it I I
mot v detat I -,I, -%-'t Ik t.it ~i m tit,. vt I #-c I (-f w-mi-k-hitt doni tit-, mol
illill"'llin" ,?I 111 " m f.( h ~l, 11 1 t a I (' I I lo I t I v~ () f III t a I '~ a t 0. 1 (,V,.% t ed t ctil p 0 t' -
atures . Cr cep t P.9 t s I,, et e c midtic t ed oil N I , v a nd A I N I) o( I tit f- n , i n
both cold-w4)rIced r vii u c t I (, it I n t it I c kri P s -4 ) I nd it it it po I -f
Card t/'j

kin lif. rw
II t
N

V

1) 41
men s
co d-wI
t t -C) ( wnI
t I

h h
Iv t,1.ct
Cr t
c0 (11 1 c e I o r-tim It I oti .
C. n r- ri /

:~/l "61(-)- 1 ~, 1 4/,), Vo-o)/c, I-)
On t 1) P p rob I 1-in o I. . - . im I ) -) / E 3 o -.-,
Ab S OC I \T i ON: ;. ii a r ' i~,) v,~ 1~ i \ , ~ i, , i oo r, t v owi v v i i n i v (, i , t t f- t
ill). %. . (,or'i(nqfi
(Khar-'~tov -tate I-nivorsitv im. A.'-I.
SUBM ITT 1-11) : F (, I t- I la r N, ~-, 8 , 1 1) 6:-,
Cnrd 3/3

PINES, 13.Ya.; h1JZf2M;OVA, R.1
Change ir, s,-ibmicroporosity I.-, fjjr.r'-rc,-,-t-c .:rr~r, filzus
foilowing annealing Lnder load. Fiz tv,-,r. tola 4 n,
My 162. 0.: 1. L!, 15: ~
1. Khar kcvski), j-,-,qudart3tvvnnyy univers:Aet i-mcni Gorlko(7o.
(Iron plating, DiffuBioW

PUMS, BAS.; SIR.61-110, A.F.
Diffusi n flow and state of nonequ!'-ibrium in cerainic
metal cautinj:s. A'zv. vyu. ucheb. zav.; chorn. met.
,6o. 15:5
1. Kharlkc,vskiy ,osuearstvcnnyy universitet.
(Diffusion)

eyinz, Map; ~IREKKO, A.F.
DeterTLimtion of diopersity and lattice diatortiom by
harmonic analysis of k-ray diffraction lines. Kristallo-
grafiia 7 no.1:20-30 ja-F 162. 0-111U. 15:2",
1. Kharlkovskiy gosudarstvennyy Lniversito Dr. A.M. .
GorIkogo.
(X-ray crystallography)
0.0

P32XS, B.4.,- SIMKO, A.F.
Determining the dispersity and lattice di6tortions in
VrIC 3tool following quenchiM and tempering. Kriotallografila
7 nc.1:12,-127 Ja-F 162. IMIIiA 15:2,
.1 univ,-)rr-' tot.
1. Kharlkovskiy :-usu6arstvern3r
(Stoel-*Pbat treadmevt) -
I latticea,
k

PINES, B.Ya.
Diffusion and mechanical propertien of solids. Usp,fiz.nauk 76
no.3019-556 Mr 162. (KIRA 15:4)
(Sol-ids) (Diffusion) 'Viscosity)

PHASE I BOOK EXPLOITATION SOV/5953
Pines, Boris Yakovlevich
Ocherki po metallofizike (Essays in Metal Physics) Khar1kov, Izd-vo
Khar1kovskogo goo. univ.,, 1961. 314 P. 50DO copies printed.
lResp. Ed.: 1. V. Smuohkov, Candidate of Physics and Mathematics;
Edos A. N. Tretlyakova; Tech. Ed.: G. P. Aleksandrova.
PURPOSE: 'This book Is Intended for scientific research workers and
engineers working In the field of metal physics and physical
metallurgy. It may also be useful to senior students specializing
in metal physics at schools of higher education.
COVERAGE: The book deals with the molecular and kinetic character-
Istles of metals and alloys. The following are examined: 1)
approximate calculations of equilibrium diagrams of metal alloys
for two-p three-, and n-component systems,, the comparison of cal-
culated and experimental diagrams, and the comparison of alloy
constants taken from diagrams with experimental thermal constants;
Card 1/10

Essays in Metal Physics (Cont.)
SOV/5953
2) the evaluation of surface tension of metals and alloyB# in-
cluding interphase surface tensiono with adsorption effects
taken into account; 3) various phenomena connected with the mar.-
Ifestations of self-diffusion of metals and alloys, such as sinter'
recrystallizations diffusion creep, and delayed fracture; 4) tht,
phenomena of diffusion in alloys and their effects (the Prenlra-,
and Kirkendall effects, the effect of orystal-lattice distortion C-ri
diffusion, etc.), The book In based to a considerable extent on
results of investigations carried out by the author in cooperatior
with A. I. Bublik, Ya. Ye. Oeguzinp A. P. Sirenkov I. V. Smushkov,
and R. F. Chaykovskly all of whom are faculty members at Khar1kov
University, There ar; 134 referencesp mostly Soviet.
TAWZ OF CONM!RNTS:
Foreword
Introduction
7
Card 2/$

a t
is --ferert .r-. c as t e.-
~Ln,-ent r~k t i 3n d e c r. c e
v a e s h -- c c n t r ~, t
r,A t f ZI t :n r ~, r I 1:.,l t, EC,
f C: v c~,.-Acc. ,,t rat i L: E: :,, i c
t ra t i z: r. 3f t 1 3 c I f c
n:cKe: c 3 n c en t r a t e a s e s f r c,.-. t D
c 5- t t zj~
-13 as es
S, le;ht.- and log(
Cari 112

a:', C U
e 3 b e L m 0 c a rl
In a lo.lz 1

(
j
(~

c.
r ~~e e 0
E~c

L 0 1
e
e- 0
r
j o
Of'
r
0
r, e or's
3
S
z 0.
S 00 _f, of.5
5
, 4r
I t5 8r 0
OM r

tl t
96
5, 9 . r
r
'30, T 9 e

ate
Q a t of,
r

15 ..Be c
t
or,
e

Lj

c cc, r, ra t t' n
77 !3 t r, L. v u
C '0"
ZZ
ex K -
z r, a D r
1. F.':' e :3
t
e
ti EL er. ori.y o e a co
is t , e ne at om is
t
r. t~z. ri e r V~rt'x .n atom c1, x
3 e. r So t :.a" Z-Z LC -C
d Jr. Ua 0 t 0 r. I a 0 a . ex'-
f
AFO -(z C.)' U.-4-c,',U..---- 2c,(l

t 61 t u h
C - t q j, I- e b t a i r. o a r 3::.
e xP Vf Y'] U,.C.;
L
ic.
M exp (z - Z~ Uc.,,.;
c kf L 2 N,Ni
Dc, M exp (z - Z) uc.til;
f4i Ucc. -*- I J/
Dl'~ Alexp z - Z'
N, L
D C,:
Dr;, =exp (q, - - qc.),.
C.
Dcc: (9N,, - qc.)" (9a)
-;~-Nl = exP
DN,
exp 9,c.),
kT N
Sara

z- 2 E Z-Z'
t: r u tt r v
-ars'v,;~nnjj r.4-versi 'et K
n v SS v (j a 7. e r. r
tru C r
CIF
L e
ri me n calcu.ater, e i~ r
a x Pe a o urv t! s
a d a al c,,i it t e d r, d 4 i 3 r I;M
-a-
f C 0 e f fC i e r, t 13 0- Ij N i )aa dependent or, tne Ni concer-

0- 2, ~,) V- 4 2 3 /j- 3
B 102/3 134
Ya &r.] Sirerk.,)
oncenlrat-~)n :e~enlenco of cree-., an,' ~ongevlty under
:Oaj of Metb: alloys of t,,e systezs .:-on carbon and
co-).,o~z at elevated tomperatureb
7-zika tverd.~j-,o tela, v. 4, no. 7, ItU,
,--ncontration lopendences of t.1,e mechanical .ro,)er,..,!s
e aloys zero Ptudiol in cast ind spec imens .
I - : 6, ~J.4o an(i 1, ,.0 f w i t h
e for7er :.ontanel < 3.02 ~'"rmcoj, %J.Q
rj' (-03T(380-',3)' for the types of
I f- s a c c o r~ r, to r DGT '38 -
)U A.
T. 4 n 10 kld 3 t 1 a t t or
e ~T-5 %"1'3-5~ J Y
specimens were
c -j r, e J U- . j 5 , 3. 1 0.3, 0.' and 3 . 13?4 of 0. Al:
~,m Ion,: and had a cross section of 2.5-2 .5 mm2. ',he measurements ivere
.7.a-4e -at 730-IIJCOC. "..-4e Pe-Cu specimens (Game size) viero )reaBoJ from
I in eight
Armco-iron pouder and electrolytic Cu ~grain size < 50 A)
d,4fforent concentrations. ;,fter sintering at high temperatures the
Oard 1/3

dependence of creep 2,'13 1 43 4
beve carrivi out anler Bt-,CUqOq 3f -l)JJ &,'MM U~ V
J 0 C .Res~~ Its : I n ?9-C al 1 D, a the creep rate is pro,,o.-t ional
'.G e c3efficient at all temperatures and concentritions.
vias observed a, Fe - Cu.
L, L~:: E, *endency In Fe - Cu alloys the con-
centratiDn JeDen~ence of t,:o creep rate is a non-linear function at all
e r "urea it in always lower than would be implied by a linear law.
"-4 of t.-.e different type of
fact is ttributed to a boundary effect a
7~-,e creep rate V is a pover function of the stress
'or Fe-C n - 4.G, for Fe-Ou n - 4.3-4-5. As regards stresses
-h are not too small , th is is in agreement wi th experim enta 1 Jat a
n first approximation log Vi is independent of stress and temperature
7
_onzevity under stress) but deoende on the structural state ~ni
cDncentratior, of the alloy. It difiers Creatly for cast and powder-
ZetL: specimens of the name concentrat ior. and depends -,reatl~r ~n
t,,* hGQt treatment. For IN - m~u d1loye, log Vi varies moat strongly in
.7.e sin.-Ile-phased regions and wea?'y In the two-phaaed regions of the
eqailibrium, Ji.agram. The approximate constancy of log Vi is not in-
consistent rith the relation V - Dp n and that obtained for i by Pines
Card 2/3

3/18 1/62/004/007/025/~,57
n e r z i oj-, jepeadence of creep B I 02/B 104
2t 5, 11,V'/ - ...
"ore are 11 f; req.
Knar'kovskiy i-ow, Jars tvenryy LA,-.-vt:.-sitet i:.,.
(K-harlkov State University ;menll ~orlkiy)
~.arc- )62
Card 3/3

A
lp

PINFS, B.Ya.
Kinetics of sintering in the solid phane. Fiz. met. i metalloved.
16 no,4:557-Wo 0 163. (MIRA 16: 12 )
1. Khar'kovqkiy voslidlirstvennyy uhiversit,st Lmeni Gorlkofo.

PINES, B.Ya.; GREBENNIY, I.P.
High-temperature electron diffraction apparatus with three magnetic
lenses and an evaporative chamber. rrib. i tek~,. eksp. 6 no.l:
156-160 ja-F 161. (JVdRA 14-9)
1. Khar*kovskiy gosudarstvennyy universitet.
(Electron diffraction apparatus)

S/(Ir l,'076/003/004/CO5
El c2
A117;l DR: Pi TI Y 'I
7 T
q
10 1) 1 C it L lla,-ek~, i f i -;,I i
T Or th,~ b a a 1 9 u ro ci,-i f r m ri,,! ow han
been ~nmril s~d on 'he il fur, ',i n w).1 ! ) o ~iecl,, -in 1 -1: r-1,1, rtl ell of no, idn
There are 1 7 fl 6,arf~j an I or-icoig Sc vi ot wil (it
Card 1/1

PINESP B.Ya.; SIVOCIIUB, V.A.
Structural changes in copper sIngle crystals ii~ high-temperatire
creep. Fiz. tver. tela 3 no.9:2703-271.1 S 161. (MIRA 14-9)
1. KharIkovskiy gosudaratvennyy univerettat imeni A.M. Gorlkogo.
(Copper crystals', ~ (Creep of metals)

A VTHOPS P
I I TLE III f! I e I e I lit I I],%
A I'l t It I ~ e I..,
forals of Ille
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5/0,10/02/00-, /0c, /Oc. "/Cj~
E I 12/E'tCO
Siz enku . It F
t I oil o f t 11 v II~Ief~loo 'syl( 11" .1 , 1,11
vivan!4 of tile 11.11 1111,111 in.liIN-i- I 't,
X - ra N, powder I I fie!'
PERIODI(AL KI I ; ta I I ogi t f I ,-,% v 7 Ito I , 16 -10 W
TEXT Xn eximmit ion 1 9 ma(ie of the et r ir s a r I !~ I n i, I it ll,~
Four i et :i n.A I v .9 1 s o f t h e f o r in o f 1 1 ri e sI n an X - r a N Iow (It- i ph 1 ~L t I
1) c , it ti 4 e o f t lie inexac ~ separat ion of tile I I ne I r um t h (? 1 1% g! it riA
I I s ~,i I I- w n t I ia errors of I !ii s kind I ea d t o i pa ra I I e I
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t?ffi ,ic- n1 r ek k on e d c) v e r in 1 ti f in i t e I nt 4- 1v, iI a TI, I tlie
c I I -n r c, t r e ipunci i ng t ,a f in i t e in te i va I o~ul,d I iq i ,Y4 f L)r
I e .1 e C) f lie Call, 11% , lit ve I II'l 011tik e '1 [1.1 t -A C_ AI- rn ' t I
f the u i d i na t e s u f t 11 e ~ It r v c- i - I c) g A - / ( n ) l- I I t v I
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C a I li I /

S/U-0/6_1/007/UG I /C)() 71/(,_
T h c- d c- I i r.,i I i j n of E 112 /F 4 60
o f i I I C..I , -. in f '. 1) t. III (I '' f til I xf-d I ype %flowo,I I Il'I t I Il. I ')I
of th- v\pur i men I I I , oil s I r it ( t e (I t tit ve o f (i t-, It I I
f z nn I ) i e , . I I . u I I e d one I I wa v s I e I d !i. I o a pa r I It i I j o-m, Fi
t he or d i na I e of t lie c ur % v On t h I it ti-i ~ 1 4 -1 v on f, I I I In--- t ho(i
,-I n.-i I y.,; I ri iz it n Interferen(e I t n e I pl, ca r m to 1, c- Ihe c ons I. r i I - t I _ ri
h e F ou r i e r II n s IF o r m a n d t 1) o it 1, r o x I ma t i. o ti I~ v t Ile f,in. t I un
t , - Mn Nn2 t o t lie a I tj e -4 found f or I I og %It
opff i ien, M snd N in he found fr om t he exper I Y- n I
of If f_ I a I I i n I e g r it I v a I i i p ~i f It ex. elit n C)
'ho! p it f I vu r e it a n (I I la~ Ip
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M (toi ko c, Kh.. I k 5 1 li Vti i r i I N i
S, ( B M I T, r F, D F
Ca r I -, / -1

PINES, bjo.i CHAYKOVSKIY, E.F.
Does diffusion in metals accelerate or retard plastic deformation?
Fiz. met. i metalloved. 11 no. 5:812-841 My 161. (MLRA 14: 5)
1. Kharlkcvskiy gosudaretvennyy universitet imeni A.M. GorIkogo.
(meta.Uography) (Deformations (Mechanics))

s 70 -mat. nauk, otv. red.;
-'-_AqyjVYlCb; R(UMOV, I.V.,, kand. fiz.
I
TRETIYAKOVA, A.V., rod.; ALEKWIDROVA, G.F., takhn. red.
[Pb7sical met&llurgy) Ochorki po metaUofizike. Kharlkov, lzd-vo
Kharlkovskogo goa.univ. im. A.M.Gorlkogo, 1961. 314 P.
(MIRA 14:12)
(PlWsical metaUurgy)

PINES, B.Ya.; KUZMSOVA, R.I.
Variation of ffubaLicroporosity in electrolytic metal-lic film during
heating and under load. fiz.tyer.tels 3 no.5:1475-14& )?y 161.
(K[RA 14:6)
1, Kbarskovskiy gosudarstysmayy universitst Imeni A.M,Gorlkogo.
(Porosity) (Flectr-ocbwdcal analysis)

L I I 'I P 1-~ , ) " 3 1 ~, ~ 91111 17
3~
S/07o/61/006/006/003/008
E132/E135
AUTHoRS Pine_m, B,Ya., and Gumen, N.M.
TITLE An X-ray qtudy of cobalt ferrite whizh has unflerz-_~n~
thermomagnetlc treatment
PERIODICAL Krista'lografiya no.b. 1961, 901 906
. I plate
TEXT; It --a shown that CoFe2O4 of B*rlctly s*c-hinmei-,
,omposition does not show magnetostrictive or structural changi,-*
after anneal~~ng in a magnetic field (TMO). The condition-, use'
w,!,Te annealing in N2 at 300 OC for 3 hours in a field of "000
~'611owed by ccoling under the same conditions a* 100 OC/hou-.
In the ox*dised state (0 5% extra combined oxygen) cobalt ferritp
3hOWed an increased value of the magnetostrictive saturation an-J
a lowered lattice constant (by comparLson with the :)mposition
CoFe204). After TMO the ferrite had develeped a uniax,~a! magne-
texture dire:tly connected with the presence of ex::ess oxygen.
In this state the coefficient of magnetcstrictive saturation
whL:h depends on angle according to
Card 01/1 * a,, Bin2 0 al - a2) S
I/ ~

It_, 7 ?
AnX 78Y study of -(~bai, ferrite S/0'70/6 1/00f I 00ti (),j Ito
F 112/E 13'
Wh P A 2 X 0.4 q
[1001
2 2
S a 5 wit P r e 1 3 t1d it h , I P
,)q -nes - f lie akagne sek % icn ve ~ t or and he d P ', i on c-
me n c f X 7 e lat I'- to the cube axes I* an be t, n j t- 1
lid t h z- dii-format ~on of the Intl ice a' er I MO c (, n i i % n o -i
a -hanKi? of dimensions and shape )I the Unit ~ P I I h.1 "I;)
a q C a hange in the posit ions of the iento Co and P - r la
- h , 0 - o ns , This requires v e r i I I c a t ion by mrag,jr i n X v
--~f I-x n intiensties in iinglp ' r v i t a I g b P r ? a nd a P
rhpr P a- . 4 figurps an.,~ 14 r e, fe r V ric e 8 4 a ri'l
S-vipt L". The four n)(,-%t , *-nt Engl:.,%Ii .1anguage re-,- f,n
11 te P Pe nn Y e L. 11 Hi k1or (1, Phvt% UP-, . vo 1()A
21- lip, -
1 1, It 11; _kfvrrj j . M 11;~ own
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4 1,' W i I I . a ms R V. It e I e n r e h E A. Ne,411
J APO. Ph V~q Vc 2 8r 814 1

U''72
An X-rav study of zobal' ferrite,- S/070/61/OOb/00b/('('l,/ooO
Re f'. I IK.M. Mer rJ Appl. Phym, vol.~l 1 14' 1'4~,()
ASSMIATION Kliny 'hovskiv gosu(inf-mtvpllllvv Ullivel-41te, ~m
A M. Gor kogG
fKhar,kov State University imen- A M. Gur ki%)
SUBMITTED June t) l9bi
Card 1/2

PINES ,-B. Ya.--
Directirr.t.1 self-diffusi-r. ir solids under t.-p ef'ect of
temp-rpti-rp gradlents. Fiz. met.imetallov. 11 no.6:04F-Gel
Je 161. (MIRA 14:6)
1. Khar'krvs'kiv ronudarstvenn universitet imeni 4. 1-%Gor'k(go.
(Diffusionf*
(Met-als, Effect of tempemUre on)

i'INF.S, B.Ya.; i.,RJSHKGV, I.V.
Coefficients of self-diffusion in ulloys. Fiz. Lver. tela 3
no.1:146-153 ja 161. (MIRA 14:3)
1. Khartkovokiy gosudurstvonnyy univorsitet im.A.14.Gorlkogo.
(Diffusion) (Alloys)

lq-da-L 9/9 P-3
qu
-,-47 _'Y'A P- 'ITi-, '-V'A ';'rU -All
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PINIS. B.Th.
Xinetics of sintering in the solid phase. Fiz. met. i metalloved.
10 no.5:750-755 9 160. (KIRA 14:1)
1. Kharlkovskly gosudaretvennyy univereltet imeni A.M. Gorlkogo.
(Sintering)

S/126/61/011/001/003/019
E111/E452
AUTHORS: Pines, B.Ya. and
,TITLE: of eatigation of
-Cold-Deformed
~haykovskiy, E.F.
the Kinetics of the
Iron
mqtsll01d*niyo,
Rqcrystallizationl~
*PERIODICAL: Fizika m*tallv
pp-34-39
1961, Vol.11, No.1,
TEXT: The authors, with Kaluzhinova (Ref.1), have shown that in
the initial stage of low-temperature annealing of copper very rapid
block growth occurs, explicable on the basis of a dislocation
mechanisin (polygonization); furthei- block growth after high
temperature annealing is due to diffvsional collective
recrystallization. The object of the present work was to see
whether similar effects occur in other metals, particularly Arnco
iron. Zh.V.Skuratovska a, G.V.Ptitayn and V.G,Krivko participated
L
in the work, which was carried out as before (Ref.1). In the first
part the relation between linear block size (e.g. L,0 and the
degree of plastic deformation (c,% ) was found. This is shown in
Fig.1 for deformations up to about 70%. In the next stage, block
growth kinetics in isothermal annealing at 600 to 1000*c of
specimens plastically deformed approximately to 50% were studied.
Card 1/5

S/126/6i/oii/ooi/003/019
Elll/E452
Investigation of the Kinetics of the Recrystallization of Cold-
Deformed Iron
Before X-ray examination,specimens were etched with 5% alcoholic
nitric acid. 200-micron diameter capillaries were used for
specimens annealed up to 8900C and larger diameters (up to 560
microns) for higher temperatures. The work showed that specimens
50% deformed and having an initial block size of about 0.4 microns
showed, after annealing at 600, 700, 800 or 890*C for periods of
5 seconds to 20 hours, effecti similar to those found for copper
(Ref.1); in the initial stages, blocks of about 4 microns are
rapidly formed. The activation energy for this rapid block growth
is estimated at 41000 cal/g atom. An with copper. further block
growth or prolonged high-temperature annealing is diffusional in
character. Fig.2 shows dependence of block dimension (L,~L) on
isothermal annealing time (Vt, hra); the graphs 1, 2 and 3
relate to the annealing temperatures 890, 950 and 1000*C
respectively. Activation energies for this process are 51 kcal/g.at
at 700, 800 and 890*C and 68.4 at 950 and 10000C. Changes in
14 econdary extinction accompanying the diffusional growth were
measured as previously (Ref.1) with a type YPC-5()L4 (URS-501)
Card 2/5

S/126/61/011/001/003/019
EIII/E452
Investigation of the Kinetics of the Recrystallization of Cold-
!Deformed Iron
!apparatus. Fig-3 shown changes in integral Intensity I for (110)
band (220) lines with respect to block size ft,~O at 700, 800 and
!890'C (curves 1, 2 and 3 respectively). Block mime was found by
.the micro-boom method; the authors discuss the inherent errors.
Fig.4 shows relative errors as functions of block size (L,u) for
;two sizes of capillary used in the determination and for two
different absolute errors (Curve 1. &N = 3, capillary 200 u;
Curve 2, ANN = 1, capillary 200 u; Curve 3, 46N a 3, capillary
56 u; Curve 4, &N w 1, capillary 560 u). An the dimension rises
from 3 to 5.5 microns, the error rises tenfold. There are
4 figures, I table and 7 references: 5 Soviet and 2 non-Soviet.
ASSOCIATION: Kharlkovskiy gosudarstvennyy universitet im. A.M.Gorlktqp
(Khor1kov State University imeni A.M.Gorlkiy)
SUBMITTED- May 26. ig6o Z5
Card 3/5

S/126/61/011/001/003/019
Eill/Z432
Investigation of the Kinetics of the Recrystallization, of Cold-
Deformed Iron
(91
A.
-5
Card

S/126/61/011/001/003/019
Elll/E452
,Investigation of t he Kinetics of the Recrystallization of Cold-
,Deformed Iron
Pitc. 3. 113veptepyie mmrpajibnoa
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11MITHMHOMS
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Fig.3.
Card 5/5
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J

S/181/61/003/001/017/-~42
B006/BO56
AUTHORSt Pines, B. Ya. and Smushkov, 1. V.
TITLE: Self-diffusion coofficientn in alloys
PERIODICALt Fizika tverdogo tela, v. 3, no. 1, 1961, 146_ir~
TEM The present paper deals with a theoretical estimation of Ine self
diffusion coefficien t Dad of the i-th component of an allay. The studies
i
are based upon the following equations of the diffusion theoryt For the
flux of the i-th component, q,. -Dijc,/~x holds, where ci denotes the
concentration and DI the diffusion coefficient of the componenti Di is a
partial diffusion coefficient. The "mean" heterodiffusion coefficient of
sd
a binary alloy is given by D - c1D2 + c2D1, D i is related to Di ,Which is
a1so described as being a partlal self-diffusion coefficient, by th'.
relatior (3)t D Dad (1+31n fi/~lr, c where f, is the activity
Card 1/5

S/181j61/0O!/001/017/0,' 2
Self-diffusion coefficients in alloys B006/BO56
coefficient of the i-th component. If the solid solution Is regular.
D Dad 1 _ 2UO C(1_0) holds, where U Is the mixing energy of the
I I kT 1 0
alloy. For describing the heterodiffuslon, it is therefore necessary to
ad ad
know D I. The estimation of D I is carried out for various simple c4ses.
First, a binary alloy of inhomogeneous concentration distribut~-_n is
studied; A is assumed to contain a radioactive isotope of the concentra-
tion c 1(x); the non-radioactive isotopes of the component A have the
concentration c 2(x); the component B has the concentration (1-c), where
0 - C +C 2' For the volume flux of the radioactive atoms one obtains%
2 do dck )
+ c or c do~)dcl , where 4 is the inter-
dx 1 di ldc1 dx
atomic distance, and CAis the concentrution-dependent transition probabi-
lity of a radioactive atom from one plane to another at the distance
The cases are now investigated, in which cl(x) and c 2~x are variable, but
_12 ~cj
C - C 1+ (17 is constant. The following is obtainedi Gk dx 'where
Card 2/ 5

S / 18 1/61 /00 1 A 17 10,42
Self-diffusion coefficients in alloys B006/BO56
Dad (c) - -12aL is the "radioisotopic" self-diffusion coefficient. If also
A ad dD d d
dc
c-c(x), then JD (c) + c As Tc If c =0 and ciftLc, then
dc dx
ad
Dad (a) 0dDk 1 dc If c .0 and c,.c, the partial heterodiffusion
A 77J Tx 2
coefficient is defined by D hd (c) - Ded + c (11). From and
A A (c) dc
(3) one obtains Do d(c) - DB d(1)f(c), where DS d(1) Is the self-Jilfi;s.-n
A A A
coefficient in pure metal. If the Interatomic distance is a function cf
concentration, Da d (c) 2(1) Dad (1)f(c), where i(1) is the interatomic
A 2(c~ A V/
distance in the pure metal A. In a regular solid solution, the activity
coefficient f(c) - exp Uo (,_c)2, and one obtains
kT
Card 3/5

S11811611002,100110171042
Self-diffusion coefficients in alloys B006/BO56
Dad (C D exp where q is the activation er,--gy of'
A A oA I kT A
self-diffusion in pure metal. Aproximatively, D8d= S2 Vexp(As/k), wner-? V
C
is the frequency of atomic vibrations, and As is the entropy of self-
diffusion activation, DO.D OA' For diffusion in infinite dil-itior. (_ A.
d
QA(O) - QA (1) - U 0 holds. If by D8 .c 1D1+ C2D 2 one denotes the coefi'tcent
of self-diffusion of "averaged" alloy atoms, one obtains the following
relation in the approximation of the regular solutiont
Dsd.c Dad 21+ ad Uo(1-C ) 2; and f:)r the activation
A A (1-c ) C D (1)exp I
(')exppkT A B B kT B
energy of self-diffusion of the alloy it follows t ~at
ad llnD'd cAI) oA 14A -U0(1-CA)2] exp +
alloy' - - D8d (1-c 2
1~kT) U (1-CB)2 exp Uo B1
CBI)oB[qp- 0 XT
Dad
Card 4/5

S/161/61/:~:3/~,--1/017/042
Self-diffusion coefficients in alloys K'06/B_-56
Q as a function of Al concentration for an Ag-Al alloy is calculated from
the last-mentioned formula, and Is compared with experimental data.
Agreement, especially for small concentrations, is good. There are 1 fi-
gure and 10 referencess 8 Soviet-bloc and 2 non-Soviet-bloc.
ASSOCIATICITt Kharlkovskiy gosudarstvennyy universitet im. A. M. ~;cr'kngo
(Khar1kov State University imeni A. M. Gcr'k1y)
SUBMITTEDt May 27, 1960 J
Card 5/5

S/126/60/010/006/014/022
E193/E483
AUTHORS: _9Aa,&p Grebennik 1,P and Smushkov I V
Ya
TITLE: Electron and X-Ray Diffraction Studies of the
Heterodiffusion Coefficients in the Nickel-Chromium
System
PERIODICAL: FizIka metallov I tnetallovodenxye 1960 Vol 10, No h
pp.879-885
TEXT: In the first stage of the present investigation the
heterodiffusion in the Ni-Cr system was studied with the aid of a
high-temperature electron diffraction camera The experimental
specimens were prepared by vacuum deposition, an NaC1 subFitrate
having been used to deposit consecutive layers of quartz. nickel
chromium and quartz, (The layers of quartz served to prevent
preferential oxidation of chromium during the diffus ton annealing)
The total thickness of the Cr-Ni layer was 1,7 x 10- cm, chromium
having been deposited In such a quantity that on the completion of
the diffusion annealing an alloy, containing 20 to 25 at,% Cr
was formed. Two variants of the specimens were made
(1) "equilibrium" nickel -"equilibrium" chromium and
(2) "equilibrium" nickel -non-equilibrium" chromium The vari.int
Card 1,A

S/126/60/010/006/014/022
E193/E483
Electron and X-Ray Diffraction Studies of the Het erodi f fu-;j -n
Coefficients in the Nickel-Chromium System
(1) specimens were prepared by rapid deposition of nickel from
strongly super-heated source on to a mubstrate pre-heated to
about 4000C, followed by rapid deposition of chromium on to the
nickel layer whose temperature was about 3001C To produce the
variant (2) specimens, nickel was deposited in the same way as in
variant (1) but was allowed to cool to room temperature before th- V/
deposition of chromium was carried out, The electron diffraction
pattern of the variant (1) specimens consisted of two systems of
narrow lines, whereas those obtained for variant (2) specimens had
narrow nickel lines and diffuse chromium lines, The mean value of
the diffusion coefficient D for the variant (1) sye--Imens vari(-1
from 24.1 x 10-15 cm2/sec at 60CC to 0,415 x 10 5 cm2/.-;e,. at
520OC; in the case of the variant (2) specimens. D varieci from
48.2 x 10-19 CM2/sec at 550*C to 2.41 x 10-15 cm2/sec at 450'C
The activation energy for diffusion and the pre exponential
calculated from these data. were Q - 51500 cal/mol and
DO = 0,18 CM2/sec for the variant (1) specimens. the corrp,;ponklin-,
Card 2/4

-;/1 L'O It' 010101'()0(, 1 U I 14/0__
E I 1,3/E483
Electron and X-Ray Di ff ra( t ton Studl es of the Net erodi I t,j!~jon
Coefficients in the Nickel-Chromium SyqtPm
values for the variant (2) specimens being 14000 _01/mol 'ind
1.6 x 10-5 cm2/sec, The specimens used for X-ray diffraction
analysis consisted of 1.5 mm thick discs of electrolyt)c nj;-kpl
(vacuum-annealed at 14001C) on which a 5 to 6 micron thick layet c~f
chromium had been electrodeposited The diffusion annealing
(at 700, 800 and 9000C) was carried out in a bath of molt(,n b0ii
oxide. The concentration-dependence of D , determined by X-rty
diffraction, was similar for all three test temperatures
D decreasing with increasing concentration of chromium At 900'(-
D decreased from approximately I x 10-10 cm2/sec at 4 at % Cr t,,
0.3 x 10-10 cm2/sec at 33 at,% Cr The activation energy Q
varied between 30 and 40 kcal/mol the Q versus concentration
curve having a maximum of 40 kcal/mol at 18% Cr and a local
minimum of 33.5 kcal/mol at 30% Cr The Do versus concentration
curve also passed through a maximum at about 18% Cr The graph
illustrating the relationship between log D and I/T and
constructed from data obtained bv electron diffraction )n tht-
Card 3/4

s/t2b/60/olo/006/014/0~2_'
EJ91/E483
Electron and X-Ray Diff ract ion St t1dips; of the fleterodi f fit-; 1m)
Coefficients in the Nickel -Chr-mimi, Symtvitt
variant (1) specimens anti by X-ray diff-roction on elec frolyti,
specimens, constituted a single straight line. indi,ating it -Io-
agreement between the results obtained by both methods. Fh.P
students Yu.Krot, V,Solunskiy and D,Sherman partic1pate(I in th-
work. There are 6 figures 3 tables and 11 references
9 Soviet and 2 non-Soviet (one of which is translated into Russiaril
ASSOCIATION. Khar kovskiy gosudarstvennyy uxtlversitet Imeni
A.M.Gor-kogo (Khar ko%, State University 1111eni
A,M,Gor kiy)
SUBMITTED. 161arch 11, 1960
Card 4/4

PINUS, B.ya.; ON LVI BEN
InveatigDting internal friction in ceramic metals. Part 5-
4ffect deternining plastic deformation nt low temperntijrofi.
Yiz.net.i metalloved. 10 no.1:58-62 J1 '60. (MIRA I ;;,,,)
1. Kharkovskiy gowidarstvannyy univerBitat Jr). A.M.Gor'kogo.
(Metals at low tompornture) (Ceramic --iatp-IB)

85968
S/126/60/010/005/018/030
E193/E483
AUTHOR: Pines, D.Ya.
'TITLE.- On the Kinetics of Sintering in a Solid Phase
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol.10, No.5,
pp-750-755
TEXTt A critical analysis is presented of the phenomena which
had been investigated by Lifahits and Slezov (Ref.1) and Garber et
al (Ref.2). In the former case the kinetics of decomposition of
a super-saturated solid solution was studied, with particular
reference to the late stages of 1he process during which
coalescence of the grains takes place. New laws were established
regarding the time dependence of the maximum radius of the
precipitated "inclusions" and of the degree of super-saturation of
solid solutions. The theory postulated by Lifshits and Slezov was
applied to elucidate the mechanism of sintering of metal powders
and it was shown that this process can be regarded as consisting of
two counter-current phenomena: (1) growth of pores ("void crystals")
and their coalescence in regions distant from the grain-boundaries,
and (2) "dissolution" of pores accompanied by ejectlon of vacancies
Card 1/3

85968
S/126/60/010/005/018/030
E193/E483
On the Kinetics of Sintering in a Solid Phase
(from the super-saturated solution), which then diffused to the
external boundary of the particle where so-called ''sintered skin" is
formed. In the latter case, the time-dependence of the process
of sIntering and coalescence of pores in rock salt was
experimentally determined, the results confirming the theoretical
predictions made by Lifshits and Slezov. The present author shows
that expressions derived by the latter workers are valid only If
it is assumed that, parallel to sintering and coalescence,
decomposition of the super-saturated solid solution takes place
and derives an expression for the time-dependence of the thickness
Of the sintered skin, which is simpler than that derived by
Lifshits and Slezov. He also shows that the mechanism of
sintering, discussed by these workers, is not applicable to
powders such an are used in powder metallurgy, being valid only for
materials which are initially pore-free and which become porous
only after heating, during which formation of a super-saturated
solution of vacancies takes place followed by ejection of the
excess vacancies from the solution. The implications of the
Card 2/3

85968
S/126/60/010/005/018/030
E193/E483
On the Kinetics of Sintering in a Solid Phase
difference between these two processes are discussed in detail and
it in suggested that, to avoid confusion, the process associated
with the dissolution and precipitation of vacancies should be
referred to as "precipitation sintering". There are 8 Soviet
references.
ASSOCIATION: Kharlkovskiy gosudarstvennyy universitet
im. A.M.Gorlkogo (Khar1kov State University
im. A.M.Gor1kiy)
Card 3/3