SCIENTIFIC ABSTRACT GEGUS, ERNO - GEGUZIN, YA.YE.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R000514610010-3
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: August 23, 2000
• Sequence Number: 10
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

&?FASj PbLI; IsAJO, Ietvan, dr,j GNGWI Erno
- I)ap3mination trace impurities in steel and cast iron. fte :!~-
K61 I-ap 96 ne.9:427-.430 S 263o
#4 1. Vasipari Kutato Intezet.
.. C

r
Ems
Investigations in the field of the solution spectrum analysis
of nonconducting substances. Kom tud kozI 20 no-3:315-321 163.
1. Vasipari Kutato Intezet, Budapest.
T~ -

GEGUS, Erno
Determining the disturbing effects in the speotr= analysis
of nonconducting materials using solutions. Magy kem folyoir
70 no.l2s524-526 D 164,
1. Ircn Industry Research Institute, Budapest.

Gi G'IS, Frno
ol- ~rnoo Plement~i tri Iron nrd steel r,.- oll,
ipo-trim irvtlysin. 11t. 2. For. linp ~,A no.10-3-~o J:i 1,,)r'.
1. 1)-,):1 Inci-istry -?m~,wtrcti jrj:7Jltqt,t*-, 211(inpoit.

HURGAM/Analytical Chadetz7 - Analysis of Inorganic Sub5t&nces. E-2
Abe Joux: 30flerst Mur-013dys, No 5, 1958) 14218
Author : Zrdsy L.,, G*gM_j" Swain z.
inst : MADMWAn AcadoW ot Sciences.
Title : ftectriLl-AULIMcal Determination of the content Of NLgae-
alum.. Unc, VAUSUM and. Mwadum in Pure Aluuir= with the
Use of a Perfonted XLectrode.
Orig Pab: Act& chim. Acad. sel. hwg., 195T, 32, No 3-4, 27T-294.
Abstract: PindlY at(RdSed solution under study is Introduced into the
analytic PY thrOU44 the Internal ClAn 1 of lower electrode
in"ted In the =Uet opening of the atomizer. A comparison
is me& vith the method of direct deposition of the solution
onto Us lower eleattede with a subsevent excitation of the
Spectrum of MW dry reoldus. The new method provides gm-
ter accumeyp Maitivity and speed of analysis. StwM&rd
solutions are prepand by dissolution of Al (99.9%) in Bel;
Card 1/2
mmGW/Ana1jvtics1 Chezietry - Analysis of T.-morg-xii,7t E-2
Abe Tour.- Reftrat Zhur-Maira, No 5, 1958, 14218
to this solution are a"", vith a micropipetto, the solution
of Zu, Ng, V and Cr and oheodmi analysis in performed. A
series of solutions vas prepared with a content of the cCWO-
nents from 0-0003 to 1-0%- The spectra a,-,- photographed in a
medium Jay-22 spectrograph with a single-law illumination at
0.02 ma width of the 811t. Spectrum excitation by &park frm
Telmer generator (C - 6M pienofarm1s.. L - 0.8 microhenry;
I - 2.5 a)- C=mnicns of blackenivgs are carried out and
backStumd, is taken into account for all the elezents except
mg. Analysis is conducted according to lima (in A): Mg
I
ZT95-53 - Al 3030-08 for concentrations 0.001-0.2% Mg, and Mg
ZM.T9 - Al 3050.08 for 0.1-1T.5% Mg, Zu 3345 - Al 3050-08,
Cr 2617-26 - Al 26-52.4% V 3110-T1 - Al 3050.08. Backgmmd
determination in made in the proxWty of 3348.5 A. If width
of slit Is reduced to 0.01 me the sensitivity Of Zn dstectic-u
can be raised frm 0.02 to 0.008$. Mean er-ror of detAmaimA-
tion Cr all elements is of � 4-5%.
Card 2/2

,GMZHMs K. [Gs9dzi8p K-1
the sticking Of
Ugilg soapsuds mixed with vwdu0t 'rOr Pr&vm#ng
concirote Six" to forms. Suggegt~jd ~,y K. Geazim. Rats.
yrea. no. 41W-15 159- (HUA IA: 1)
(concrete slab#) (Conerate-Formwork)

GEGUSI Brno (Budapest XIO Yehervari ut. 130)
-r-quick spectrochanical solution method for investigating blast
furnace and open hearth slags. Acta chimica Hun 28 n0-1,3:65-74
16le IEM 10:9)
1. 11senforochungsinstitut, Budapest.
(Spectrum analysis) (Blast furnaces)
(Open-hearth process) (Slag)

S'.
IrIolo,lye strciteli Volgo-Dona Youne builder: of the Volf'o-Don Cunali.
Moskva, Mol daia ryardita, 1~62. 56 p.
I-Ionthl L1,1j. nf gj-.r-qinn A~np-jnnq, Vol. 7 No. 2 May 1',Ir

CFGU'I'iI:. S.
liaehe komsomol'skoe del* (Our Commist Youth work). Moskva, "Molo.lsia cvardiia." 1954.
24 p.
SO: Monthly List of Rusainn Accessions, Vol ?. No 9, Doc 1954

G(ILTSUT, N.; GBMIN, S.; ZKONCHOT. L., red.; SHUTALOV, L. takhn. red.
(Istle catch up with Awrica!] DoComis Amriku. [Nooky&] Ind-To
TeX VIKSK 09olodaia Cmrdiia,w 1958. 191 P. (KIM 1117)
(Agriculture)

TAXOTIJV, T.; GIGULVjhj6jWIN. T., red.; TROYANOVSKATA, N.. takhn.red.
[Lights of Sokolins Hill; brigades of Comomnist labor] Ogn1 gory
Sokolinol; o brigadakh kommanistichookogo truda. Moskva. Goo.
Isd-vo polit.lit-ry, 1959. 30 p. (KIM 12:4)
(Labor and laboring classes)

ZIRZYV, AleksBndr Terentlysvic~: %WW, Semen Tskovlevich; F"ISHUO
Y.Y.. red.: BIRLOT, J.P., tex2mirwi-, - --.--NP"mjw
(Ageneration's achievement] Podvig pokoleniia. Koskva, Isd-vo
'Znanie," 1938. 22 p. (Tsesoiuznoe obshchastvo po rasprostranoniiu
politichookikh i nauchnykh snanii. Ser.9, no.3, Kolodexhuals).
(Reclamation of land) (MIRA 12:2)

G;7 C-- C--z ~,, -z- % t.-,)-5. --1 f
0AWZIx, Sleep IrzmI-KjmhA~YAK0VIXV, Toviy Takovlevich; KOSTIN. T.. red.;
... *-0takhnered.
(What the October Revolution gave the peasants] Chto dale Oktiabrl-
skate revoltutstin krestlisnem. Moskva. Goo. izd-yo, 1957. 87 p.
(Agriculture) (Peasantry) (MIRA 11:2)

0060006 0 0 0 0 o 0
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4pwlq*q jwqW1 '*A W Pim see
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rA"46.
allow its :Y Ahad. NomaLS S.A X. 4
lot. =1 ).-Tbor can miting In Is tyottills
'sm Ift-ba. and Ph-fli Worse dfld food"
the beat of = The horlst caparily is The region -.1
liquid plw ON, Tbm quantillors one aseasurvol by a.
4146*0P. O&bwk fallsoriftelorr "blorls Pritsulted KKVT%&i%c
"Wastarvinews Cd hear ralow try th"astil"Jul file IAR#T If-on
UAW 1094oldlosslasit l"I.AwlAt thorsamor linfordo-fol. the
hestaffedrus. The cipil. twilolele brat W fuskm.Q, w-wo
in the v
fiquid-Oss-SOM region mail Q& the beat used in the ph.4w
charter. To dri, rise ~~rfgr 4 frilling It "" "' "'
know Q# ma function of cwwn. ().ordsol-ld-froonsthe-4.-
ser"A firpeodeave of beat e4pollify of the anliol and liquid
phas"onewarts, From the caloed. valurso(Qs stgredo;I&
It the eneW of wising in The liquiot phAw. and IT, The
rt"lly col mizing in the soli,l phAw. on the a"umption, lbt
the jolealital energy of the join. can be ripe soor as
NI(UAA12X I - a) + (17,OPJ)s + Uss(I - 4)1. *beef- 4 1.
The cown. and VA& and ot'so we The W.Ceww efteelli".4
like slows. In the Pb-.% system ('I - IAI X If)-'$ eil!
Ind. &W 17 - 1.3 X t0-11 In the hi-Cd system I'S -
11 15 X 30-68. In the 111,1-boystem, tj - O:r, X IO-Olaspi
Vj' - O.W X 10-P; file IAllet value w4% siltried by n.m. -
tquil.froodkinorts. In the III-tin system C11 - O,m x Ifl-'s
and bl' - 3V X 10-01. In the Mill system t1 - - I I
X 10-91 and IT - +8 X 10-11. Then valum prvdicitil
lkluklat and aWklw Unct; lit jand agreement with empt. ex-
cvpt for the Widus of rise ftj~% system. The C1 values
11cferd fifth rriworied order in Uquid llb,',n
.nd 1114% bat did not ogfvr with that In Mill alloyof 'the
energy of taking defol altervativotly from the "jump" in
twat orospostity during bratme through file wolodut atul liqui-
flusliftesereed well with the town" value in thr lit-%" &"*I
III,% OF00141141 but "Or III I he IIW41 -T-IfIn b-TAUW 14 WM-
equIL COMMItals A. 6. One

~/Chi6ieitry - Lead-Tin AU*yu Oct 51
"Iftergy off Mixing of Binary *tMl Alloys. 1. The
Load-Tin System," Ya. Ye. Geguzin, B. U. Pinesp
POWsicotech Inst, Acad Sci- Ukra-iniez SSR, wha
bov
*Sbur Fiz Dim" Vol XXV, No 10, yp 1228-1238
With high-temp adiabatic calorimeter of nev
6swIgn,detd temp dependence of sp heat in tran-
sition of alloy from solid to liquid state and
4std =p. Data on beat effects und malting of
'binary alloys sbvived that mp and sp beat in
region of se.1m, detd energies of =53dng In liquid
md solid pbases of Pb-Sn #YwteN. Sepa occurred
-in eqvd1 andez exptl -,.-.cmdtt ions - Constructed
equil diAmrsiz- eners of of -1 -1 of Fb avA
ft In liqaid pbase ~ and solid soln. IPI ad A ng
*4p-eed vith data from X-ray inv*Xt199ti= Of
liquid a2loy of eutectic cOn=.
3,9W7

^ 7; & - ,
U a. YA-
A"'loys
Unary metallic Alloys. 4. Svstems bismuth tin and bismuth lead.
Energy of mlxin~ of
Zhur. fiz. khim. No. 2, 1952.
9. Monthly List of Russian Accessions, Library of Congress, Uncl.
-'C' N~

Lil

VS811 111011810011 d ViSrOU11 AOW (ShIbl'ifig And ttPIP) III
irre isod m*W powdsix. Y H Ge ' L, 0-
Dvikdy Mad, Nsak 5,5..S~R, $7, W-PAIM2), -4t had
bett; shown by P. (C.4. 41, 076b~ that the equil. 0
vicancies, Co. In a nmW is dmttAftd by A conpiessive,
site", P. an not., 6C - (PisjbjjC#' wbas 8 Is 1(10 latticc
tPwIngi nerefore a difftrvol=e M vactucy Coma. would
exist bOween the end and *Wes of a itA of longth b slid
rclius R subjecW to simultan"iq tongiludined ten~dmj, PI,
wAsidewiiecPmpre=iutj,Pj. A flow of wwvicksof awais
wjWId occut that won.14 cause a rate of Ofoigrifion (111)~
M./b) - D&'(Pt - Ps)/(AnR) - (Pt - I'l)1q, wbtsej~
1
1 the time. 0 Is till! $Af diffu-*m Coeff., ). is A CrtCAAM Iincu:
distinct deti. the Cone". gTadient, and v is u c(-i:ff- of vls-~
c~3sity. An atIrdozov v rtiation Wwetn I and D hoWs 1,wr
$111ttfillgotmetalPo"dex-s. MO. dafit were obtain(11011 20-1
40-p powder of tiectfoly6c Cu anti nI Fe reduced from "e.
Preming was done In a mold 4.2 mm. in dLitn. and 7,5 n1n:
high, and prefoures up to 6 kg./sq. cm. vrere m.-Intaiv;i
und sitltrrinj If% was done at temps. of OW* (Cu) Awl 1100,
( Pe). 1(4 V1 V), - (a VI V), - ol IncrrAsrd linearly Withl
Increasing mabitatard jact%ure, P. whtte V Is the val.
The "LipLace pressure' on the pore surfaces was 3.7 kg./;
sq.cm.forCuaad2.DJ`orFe. The vivpsity was ladeperid.,
tnt of pressure. The deduced viduo-3 of spli-diffuNion cr-cm.
vvere 10-1 $q. CM./WC- bw Cu and 10-0 for Fr. DI.St tit a
In the cryst. lattice of th-, powder caused their Yalu. to
high. From the temp. dervn4ence of vismAity tile - IVIL-1
Ilon tntrgy fnf Musion wvi calcd. W 1bMv 30,M) C41 olel
I ~e And 12.CW for Cm. A. a, IV

GMUZIN, Ya. Ye.# FM;S, B. Ya. and SHUSHKOV, I.V.
"Microtension in the Crystal Lattice and Calcining Metallic Powders".
Uch. Zap, Kharlkovsk. Un-ta, T.49, Fist Otd. Fiz.41atsm. Fak., Vol. 4, PP 111-117, 1953,
Studied structural changes during the calcining proce33 by means
of X-ray armLlysis of saWles of compressed powder of electrolytic copper
and of nickel powder. The samples were calcined at various temperatures for
various periods of time in a deoxygenated atmoaFhere. Analysis indicated
that at temperatures below 40CP for copper and below 7000 for nickel,, microtension
is totally removed, and therefore these temperatures have no effect on the
calcining process. (RZhKhim, No 4j, 1955)
SO: Sun No 884s. 9 Apr 1956

~
of f

USSR
bld 4. Inti and Yo. H. In. Z%W.
Fis. 277-~M.-A TrffnWPWWWr1-o. NJ w" sur.'
rvoijiled by 0 wires of Cu (or vice yet=). the bundle was'
lustrit4l in a Cu tubtand slightly drawn down tolt"d good
coruct betwten the metals. Other Investigated Pat" we Q*
Y*Cu. Fe-Ni, and At-NJ. The assmVy was beated In H,
or In vacuum at 1040, Mk"vvI&-s show that the Inner
NJ wire lacrt*sm in dla;n. and the Cu wires decrease. The
Cv wires became rout, Graduall) the wh%A4 assembly Is,
bakcd tusethcr. , the entrw wire is Cu. the Peres appftr
In the center and the outer wir" I=mo In diam. ThusCu
Muvi Into NJ vrith a speed at 100* In vacussn of 1.3 x
IWO sq. em q'see. and In it of 18X 10-0 sq. cm,/w., but NJ
-Icei not diff"o Into Cu. 'rho ob-aved poreAlty Is explained
by gn li)crcjw In the numbv of vitcancles and consIdtfed;
Ul a Proof Q 111i vomacy the"ry at dial-01011. It Is $;Iowa
the'NctlLally that the diffosing atoins will t* those of thi
__LcLplm~ietit vrith the lower lattat h-2 of -~O.
(D
"MMOMIN

1 7
Fr
itallic Pe
The Weeks uf the sintsitag of priliwad'iii
L.11 Y Pinei wid Va E. 13cluzin. Mur. Tekh. Fs- 23.
MIMI. d cunirivt~,a ,.-c
11110C oil that hid b"1. %illtesed stepwix t" (4:1. tile
U S S rcl.tt~-i!i lwtwtot 4 prv:i~vlt 1110:11 illd
All time lo,d trmp. It %v,t-j klto-i Outt i-Owni-I C-111.ctipll
tit the infilAl start lncrcw~m. htxuly vllili timv, 1. Pof lonj~f
pe6 of 1 4.1 'Int I rWd It i~ I. f, 1] -46., w m, v '.. me kii,ctic% a
tho iiinterfi-ir ra-ri%44r~ 1-m "t 11'~ '!W ' '
ti"p J tile I atice. J. jt'lvur t2O~J.

va.
Cqj
A method of delemining the temperature of appearatice
lp tkilitutev of golid products.
x
R
zo. 122,17TOIT~-Aptvaram, of a lirwO such a%
a cuterilt: inixt.. cat, I,c ob~cri-l by the
alpe:%rante of -wniart mriting" ul :t ~rnlll Otrr of mir
mlill P11-1%C oft n thill 1,A)Irr M the -'fl(l wl a liteltillgi
V. N.'Ilc(j1lAf.U-

I
GEGUZIN, Ya. Ye., WMIONON, V.M., PINES, B.Yft-
"Laws Goverining the Sintering of Compact Metallic Powders," Uch. zap. KhGU
v. 48, TR. Fiz- otd., flo. 4, Kh. St. Univ. publication.
tz

=UZIN, Yfta'e., 'mvJuKON,Y 1-0.) PINES) B.Yn.
"Viscous Stream and Self-Diffusion (sintering and creep) in Crystalline
Bodies in Cospact Metallic Powders," Uch. zap. KhGU V. 48, Tr. Fiz. otd.,
No. 4, Kh. St. Univ. publication. / ~;~,
,y

GEGUZIII, Y?%.Ye., IMIWVI'I'jK/-.YA, T.V.
"The Applicability of The Magnetic Method of Determining the Quantity of
the Residual Austenite in High-Carbon Steels," Uch. zap. KhGU, V. 48, D:.
Fiz. otd., No. 4, Kh. St. Univ. publication, .

--A, ~ - ~ - -- -- .
; ! '.-I . - . . I
GEGUZIN, Ym.Y,2. ;%~~ I - I- I
"Sintering and Viscous Stream of Amorphous Bodies," Uch. zap. KhGU,
v. h8, Tr. Fiz. otd. Kh. St. Univ. Publication. 3

GEGUZITI, Ya_,Xp., GAL'PkMINA, L.I., PINES, B.Yt".,
Thermal Effects During the Sintering of W-tallic Powders," Uch. zap. KhGU,
v. 48, Tr. Fiz. otd., No. 4, Kh. State Univ. publication. / 05,~~

GEGUZIN, Yt%.Y(-:., FINES, B.Ym., SkWaQV, I.V.
"Microstrains in a Crystal Lattice and the Sintering of Metallic Powders,"
Uch. zap. Kh(RJ) V. 48., Tr. Fiz. otd., No. 4, Kh. St. Univ. publication, / izr~--,
e

k-Distortion of !he crypital 11110c4 and Watering of molil.
powders. L. I W rinA, Va. 9 .Gerutin, D. Va. Pines,
and 1. V. ftu;~kov'CA ,M. Gor"IrTSTRITrURN.. Kharkov).
Poklady A144. Nam, S.S.S.R. go, 20"1953)10rutcbef
Translation No. 30881.-Changes to the strcsscs and distor-
tkm In metal powders as a result of annealing were studied
The sp. beat
Vby x-ftys and SPA"t measurements
detd. during beating at 2.0 to 2.S dtgrm/rAn. with a high-
temp. adiabatic calorimeter. A Cu compact made of 00-P
r with a porosity of 2U% evolved 6.25 cal./g, with the
po*dq-
Max. rate at M' 9. 40-50-o powder with 35% porosity
I evolved 11.25 cal./g. with the inax. at 275'. 10-20-p NI
I powder with 18 porosity evolved 14.00 cal./g. with a awl
I max. Thirty-p5e powder with 10% porosity evolved 12.00
I M.A. wilhaWO'inax. This release of enargy correspouded
to decreases In s(tesses of the 2nd and Jrd kluds and was not
caused by dcctcsft In the surface am of the pores. X-ray
measurements were made on specimens 6.2 mus. In diam.
and 2 mm. long p from 40-50-is electrolytic Cu powder
or from 10-20-p NI powder. For Cu the elastic energy,
nW. from One breadth, decrensed from 4.2 X 10-2 cal./C.
to nearly zero In >400 main. at 1001. 100 min. at 1110'. 40
min. at 2W', and 10 min. at 25D'. It R diffusion proce"
caused tae dectex" to microstrems. the activation energy
was 20,000 cid./mol., close to the 12,000 cal.lmol. charac-
teristle of the LakW state of diffusive sintering. Sinee the
askroar - P were efim1naltd, at a low temp. they could have I
ilittle effect on the slatering process compared to the effect or
the k~kl`cnefgy of distortion. DistorW regions In the
IxttW could Increase the couca. of vacancies and decrease
the aktivatloss energy for self-diffusion.. A. 0. CU
I

USS R
Anterfax of Out' bodks. VA P C-SCMI'l. D44dy
Akad N4sl# 3 1) 45 18 fW~MV-MIkO thculY
TT 21
Ifir 111-1wollm of
tkics imt differ exictaii4l)y frnm the m:wKinkin 4 t4c inctling of
Capil.
latici Of (tirdillar Y 51licAte ckvi W;:rv Itclavil to dic "MAcning"
lemperatule. ulkl the "spoatalleotts" docrvaw of innc~ dUracter
w;4i wAcd- Thv capill.irici wvirr int4ted clurisiC henting at 2
r.p m ; deritaw itt (IL,mot ir w.vt undotto along the k-ngth
a,. the JAdhB. at "ity litin, 1, k r%jirc%wd ~ijr -taiqlj. whtfe
'a. I i~cmfficteot of vi-,tAity, ml v is,,~trwient
of mufact temlimi. RxIoetimcuLal dat:% nKmd kith th- rqu.itimi.
The xLwve eiltialkirt w~ss uu,tl tit (Ictcirininc th~ vicrydq of the
jjl:kv4 tiv aLlutill" th-t ~vx) erg,le'll I mull O'L V 'lo" ""I
ille entray of "a'i to lie ti A X 10, C41 /Illole.
Fof it ipherkJj prov. a, a. - (J#,14,j)4; ij..jmiY,g that A the
poro, N. hi;vc tlw mme nrilitial diamcier, a., 6v volimic ch4vC,-
Al'i V "? the 'pirrilfwn (comfiff.14a powder)CAu be. tiq'rcv~'j hv
4 Nvu.'J'3 V (I - 3./4*-.I)fi
This i:qtiplioti ti~fu~s C-xxf agrimment with the diLacometric cutvc
of th4 shrinkaffir of a jxwous glavt brAy (Ivtnwn, 1952) up to a
sinteting lvtW of I !G 'N fur , which takits pLut (of r4. - 5 X
10', Small differrucc,; tmt-".n cxp"kmntal sAd cakuhtes
cufmi (Of I"gr Wrifitit, Lit expkklr#e4 by gas r(CMIC wftbtn pocirs.
CIS,

t r?ummrl%a3 &S F.Ats. -VA. F. GC;utin &Ld
S S
intered an tb- tmo. 4 4
of dWiAOva A V,

F-i ~! ~ . I 4q, j"I I,: .
USSR/Physice-Sintering
Cord 1/1 Pub. 153-10/22
Author : Geguzin. Ya. Ye.
Title : Spheroidization of pores in porous bodies
Periodical : 2-hur. tekh. fiz.p 24, 1622-1625, Sep 1954
FD-1226
Abstract : During experimental observation of spheroidization of pores in porous
bodies during sintering it was found that the contour of pores shift
toward the center and that centers of pores shift tovard solid particles.
9be collective recrystallization occurring during sintering produces Ir-
regular contours tending to circles. Indebted to Prof. B. Y&. Pines.
Eight references including 3 foreign.
Institution :
Submitted : July 17, 1953

U Z_ i i
USSR/Physics-Allcys, Diffusion FD-1227
Card 1/1 Pub- 153-11/22
Author : Geguzin,, Ya. Te. and Pek Yen-gin
Title : Microscopic study of mutual diffusion of metals in inhomogeneous porous
bodies
Periodical : Zhur. tekh. fiz.p 24, 1626-1630j, SOP 1954
Abstract : A. model of porous materials was used for studying diffusion processes
occurring on contact surfaces between systems of Co-Ni.. Co-Fe) Cu-Pt)
Co-Pt. The metal with lower evaporation heat was found to diffuse into
the other metal. Such diffusion produces porosity in the diffusing metal.
Indebted to Prof. B. Y&. Pines. Eight references including 4 foreign.
Institution
Submitted June 17, 1953

Yz-
id X. N. anhartnito (A. M. Go. cil State
DoWady AW. Sauk S.S.S.R. 90,
C
r~c c-j,3,)war. carefully, Wked
u. (~ I nim. . ond
ftnd t VRCU pp 10 re),
the pecul;ar sttrfact chatips were studied with a m(cro4-cppC
111111 j& inicrointerfe, meter.
hemines v6lble t,n the metal. with each crpul
itaftlikelontiatitm.
vid their vvidth (liffir (nr di0trmt vtptak, b-it ar,-. inikin-
latned irt tacla The of Lhr~ 't-.-ps prc
ond rctnaht cnao vOlim thc rry,h).
J?o -3 /7
F

VA--
on
The Intettactol tensiork At (fie IYOU111try of a Rojl~j an,
N.
ttmonstrates the "packing" (it tf7.q Iquid on its c~wu 5.)!!d
1)h'ac, Le, a viltiallitmfligivell th'all all 1, a, whCre 6,3
o [lit inUffacial kimion at Ilie h~amd~r) 0, 11
the surface temotif'n ou the 1-ti"Jary -IA-v.Cum.. e, thc
wtltfacr (crtsi"ll at the Tlo, I Z;
~I rill oll"t I lttr~l wilb t!": dW 'A 't-01- I nxilfli-i 1 11
wev. pl-CCA in.;kdr ;k fill.) of liql'I'l I ;'i 1, -;.
-4.-- fir

.;41, 1 .7 .1
o

GWMIN. Ya.Ye.
- - -7
History of the Section of Solid State Physics. Uch.sap.KHGU 60:81-
512 '55s (NIMA 10:1)
(Kh,%rkov University-History)
(]Physics)

FORM OV Il(3RI,'T AVI.'Wit; V: '1 :1!
I)IfTt,fli,)r4 OF METALS.
Vrkl. AV.0. Nuk V:Z31, Vul. 100, 14 ;. 2, 21 1, Ji (116.,j p.
Ilueckv E~&A trauMaW~u In* Atomic Ei,,t"
TrxnsI. N.). 01 11 p. ( 051,).
In f, ('411 a -branj I..;L; C.A. 'I Y,c
IUW-i, J J-;-~ Irl tile rim-t1l. tfon) Wl!,!,
[hV pbam! mt!q o11"'11-4! to Iflu 1,,Aa~s njuut fiq--~ralc, I t,
u( Ii-smod W ttla s'll3w. Aa Uut (1( 0;1;411 1
11m, ro'. I.o lo wbit b !t cy ArIl"ll In thtA coo rub1c,41

.2"N. N
Cu I-pedmet;s (4.qVj~ p;;r.-) TItv -C-11117
or ,ifi;
al in. a! U cl~ 1 try f~ next
I f
lmt~j (to IWO 4 ith 1:2 - -, ill'
ind the luliu~ ttudi--d ZrA i!t.
L"'ZOastict,"v i Uvj~ c~rxv,.
came rwgf 1hr lt~p-.jk~ 1~ c ~r . tc.
by thz actIn. (j Oc L!z;,IL 4"" J:-~r cor ! fl,:~ vc.;e
.tccr wi.-, v~,Iv4 A O~c x ... fccc

tacc~! c,~cLLIIL4 nts
f.
li-h
- 1: 11 L-A
1 411,
It, I
I

- ----------
G) z tj A 6
USSR Diffusion. Sintering. E-6
Abs JOur Ref Zhur - Fizika, No 4, 1957, No 9345
Author Gegu~~Y~a.Ye-
Inst :1M-ar__kov Uni-ve-Mty, USSR
Title : Investigation of the Sintering of Mixtures of Metal Powders.
The Copper-Nickel System. Isomer Powders.
Orig Pub : Fiz. metallov I metallovedenlye, 1956, 2, No 3, 4o6_417
Abstract : Report on the results of an experimental investioation of
the time and temperature dependence of the linear shrinkage
of pressed specimens, obtained by pressing mixtures of appr)-
ximately isomer powders of copper and nickel. The experimen-
tal results were Interpreted with the aid of formulas obtai-
ned under the assumption that the observed linear shrinkage
ia a result of the summation of the shrinkages at the indi-
vidual contacts between neighboring powder particles. A con-
nection was established between the kinetics of the process
Card 1/2
777777

USSR / Diffumion. Sintering. E-6
Abs Jour : Ref Zhur - Fizika, No 4, 1957, No 9345
Abstract : of linear shrihkage and the process of (liffusion homogeniza-
tion of the mixtures. It is shown that at the early stage of
the sintering process, the mutual diffusion prevents the
shrinkage process, which is a result ofthe occurrence of dif-
fusion porosity.
Carx 2/2

949 THE NYLUTNCE OF PPYL`47 Pp
/
~
'Jv r MRDI F FIAJO-N L
FL5 itil PIJR~b i Y

Rusatan

LnierdLffusicn twV& n
rP
AW.-
-hn Jqlmv-,

was
VZZ Llso radhxad S1.7-11a, regl,lt-A
Yli STStom
W m7f~l

3/564/57/000/000/006/0?9
D258/D307
AUTHOR:
Geguzin, Yg,.~~
Rucleation'and growth of negative crystals
TITLF,:
(pores) from supersaturated solutions of
vacancies in a crystal lattice
'Rost kristallov; doklady na Pervom soveshchanii
SO.URCP,:
po roetu kriOtallovo 1956 g. Ifoscowt Isd-vo
AN SSSR9 19571 91-97
TEXT: The author derives an expression for the radius of a
critical aucjqugt
3
26
AT (4)
and for t,he -work, of its formation in a solution with'a given
Card 1/2
A-

F
Sy564/57/000/000/006/029
Nuclation and growth...
D258 D307
degree of supereaturatio
n:
6 2
Tr(53
:16 a
4 0
TT r*2
CT (7)
3 ~XkT)2 (A
Linear dimensions of a critical nucleus,can be estimated by
to
extrapolating the experimental dependence L t
t 0. Results obtained in this way are plotted. Using ex-,,,
perimental data on the magnitude of supersaturation in brass
during evalporation of zincg:,the author.concludes that spontane-,
ouB nucleation of negative orystale,has little probability.
Negative c~7.otals which are:obeervid.are probably due to the
Ther'~are 5 figures*
development of'microcracko.., e.;
Card ?/2

AUTHORS: Geguzin, Ya. Ye. and Ovcharenko, N. 14. 126-3-3/34
TITLE: Excess vai~ancii_soccurring in brass duri evaporation of
'~. (0b
zinc (in a system with a "vacancy source"
izbytochnykh vakanBiyakh, vozaikayushchikh v latuni
pri isparenii tainka (v sisteme s "istochnikom vakansiy").
PERIODICAL: "Fizika Uetallov i Metallovedeniyt! (Physics of metals
and Metallur673, 1977, Vol.IV, Eo.3, pp- 4M-406 (U.S.S.R.)
ABSTRACT: In this paper the authors aimed to follow experimentally
certain details of phenomena takin6 place in one of the types
of specimens with a "vacancy source", namely, in specimens
of' an alloy from which the volatile component is removed.
The selection was governed by the desire to follow simultan-
eously the kinetics of the coa6ulation of the excess vacancies
and the kinetics of their removal from the specimen which can
be materialised most easily on specimens of an alloy which
does contain a volatile component. Brass containing 30% zinc
was used for the investigations in the form of 20 ram long,
4 mm dia. cylindrical specimens after preliminary stabilisaticn
by annea.Ling at 820 C. The time and tempera"keure dependence
Oird 3L/2 of the decrease in vieie;4t and volume of a-brass specimens
was followed experimentally after removinG the volatile
component, i.e. the zinc. On the basis of t'he obtained

126-3-5134
Excess vacancies occurring in brass duria.- evaporation of
zinc (in a system with a "vacancy oourcell~- (Co-nt.)
results of the time dependence of the chan6es in weight and
volume of specimens, the relative quantities were evaluated
of the excess vacancies which coaLiulate in the pores and are
removed from the specimen. On the basis of metallogrephic
data of the dimensional distribution of the pores as a
function of the depth, assumptions ere iarde on the caaracter
of the distribution of the concentrations of excess vacancies.
A method is proposed for determining the concentrations of
the vacancies according to given values of 4P(,r) and AV(,r),
where A&P and AV are respectively the weight and volume
of the vacancies and r, time. By means of this method the
concentration of vacancies in the temperature range 800 to 900C
is evaluated and it is shown that,in specimens from which the
Card 2/2 volatile component is removed, the concentration of vacant
nodes differs little from the equilibrium concentration.
There are 6 figures and ? references, 5 of which are Slavic.
SUBMITTED: July 18, 1956.
ASSOCIATION: Kharkov State Uaiversity imeni A. M. Gorky.
(F:harlkovskiy Gosudarstvennyy Universitet imeni A.M. Gorlkogo)
AVAILABLE: Llbrary of Congress

AUTHOR: GeGuzin, Ya. Ye. 126-5-3-19/31
TITIZ- : M-ne-lZess Vacancies in Metals of Galvanic Origin
(0b izbytochnykh vakansiyakh v metalle Callvanicheskogo
proiskhozhdeniya)
PERIODICAL: Fiziha Metallov i Metallovedeniye, 1957, Vol 5, lqr 3,
pp 536-544 (USSR)
ABSTRACT: The problem is considered of the excess vacancies in
metals of galvanic origin on the basis of kinetic data on
their coagulation and on the kinetics of volume
compression (sintering) of porous powder presslings. The
process of formation of macroscopic pores during sinterino
of a metal with a hi6hly distorted crystal lattice was
investioated on copper of galvanic origin,procipitatcd
from an acidic bath onto a copper plate ahich vias rubbed
by a finely dispersed graphite so as to enable easy
re.:-Iloval of the depositeq copper from the base, the current
density was about 5A/dma. To detect the formation of
macrosc8pic pores the specimens viere annealed at 500, 700
and 9C0 C for one hour in a vacuum furnace. FiZ;.l, p-538,
shows Dhotos of the typical structures observed before and
after Luinealing and they show clearly the fact that macro-
Card 1/3'ecopic pores form. The experimental data obtained on the

Caec
C) Zrj
Of , 1110 t
the I-othor.l. 6zowth
C, -0. i1,12
-follc 62'0 0
0'111n -r 111CIC .0
f 0,U21 2 op IR6
9Qtjj,"Q 126 CCOP.
C
"~"r? .~,g -kille 0ck"q b0 Z-- Dozo, ein 3-2913,
,- . Q, Q C 11 0,- U
()C)o epn, Gr Qo t.
2C C 'cc] ep
C) 014z, e8, Ql b -roz co4rjjt.
s t;j x ir J 0
Q22,r~, 0,~j "r Z~ t , ij8ctI Qljri~7 1:. Of irac.1 0. aluat, -ua
-P-i ect C506 C vel- L4,11C -
Qz .7 Pozo -Z er-
t) 2000oatrzz , 2,-, h',~'j til CQ.Z, -ne
'Ic~ de Ctu ojjz~- i4'rL".r. I le(2 poz
0 aa, pe Q ..Zr
-1 1 .1 ~Veo
.500 8'-' on - e 0
0 t1r,2o 12Ce. Pop Ob!3e ?56 6L-rj (I UZ. Ca
0 C, Zle Ze zoclu pjro(j 0 1 or, 0
Of ~Cop~c P-Poc -fop -S 0
Cz'Q e rl
Po Ph cerl ,, 017 ti-
ze, PO."o.,t-i Vol "s0tille of PI - 10 .10
1z - ac ;., jr pIn tho L- ec ~.2022 Qt
-Qttp:- , I Th e
t j.. 0--i
.4&,#. F~I-ri dote
IPhello'. ZQ1n;. -e
Od . "PI b Xt ctoci eno at
'I utea O;e X"'
L 0 Jw C1
h -r0 ',-'I I! , 11 0~r " 10C,0
fop 0-1 t, 0 Pecloc, Qt t,
Car(, aQjjr he Und o4jo !~ppeczz"
? V41 U Ilkni I'u to 151'a I th zi t I Zzlin Q1 750
a t t jjj t, k!"o ti C C op, Z'87~-Qn 11 bo , ftk,~Cj Ice
G,U t 0 f or
tho Of CiI2 Ultz,, Wid'a '1"I
1,~ coppnz.
V,.Uc 1,7ZIGn . epo iv -7,10c Z,I ent
Th e 0,u U2 jj~~
vilth "'cle, -Itzi(joih of tobtf"Y--~tajj""11~ch Othe
L Q11jod IcQt. If'
Jrac 0.r
.142cle, ',,,he Pozo, O.N,-
C Q pL 022 or
42 ~~Jra
Of ~;Qt4 We i.
Ctu(lo pCI t Zo oQtaj
oppop op I (jJj t1tjjj
Poll th o Of " I, -se(j
pol ~,Ljo
hmb~~ - aP~jc
or Q ti
9a Jv Ire

1,,xces,-- Vacoxicies in Metals of Galvanic OriGin 126-5-3-19/31
oriGin was evaluated according to test data obtained in
sintering powder presslings. The determined values of
saturation and the kinetics of the chanGe of the i:iagrnitude
161A 0 of the Zener formula are in aGreement with the
co ceptions expressed in earlier work of the author and
Pines, B. Ya.(Ref.5) that the excess vacancies in the
crystal lattice are caused by "healing" of micro-
distortions of the lattice.
There are 6 figures and 14 references, 11 of which are
Soviet, 3 English.
ASSOCIATIOIT: Kharlkovskiy gosudarstvennyy universitet
Miarlkov State University)
SMITTET: Oct"ober 31, 1956
1. Metals--Porosity 2. Meta Is--8 tructura 1 analysis 3. Crystals
--lattices 4. Crystals--Distortion
Card 3/3

AUTHOR: GEGUZIN,XA.E. PA - 2286
TITLE-. in Metals and Alloys. (Dif fusionnaya
poristost' v metallakh i splavakh, Russian).
PFaIODICAL: Uspekhi Fiz.Nauk, 1957, Vol 61, Nr 2, pp 217-247 (U,3,3.R.)
Roceived: 4 / 1957 Reviewed: 5 / 1957
ABSTRACT: The present survey discusses essentially the experimental investiga-
tions of the creation of diffusion porosity and some phenomena con-
nected therewith. The survey is arranged as follows:
=rrusion or such metals, the ndeB -goovermnlingthhe oceurr-enoe of dif-
fusion porosity. Granulation of the pores. Modification of the
voltaic of the diffusion sample on the occasion of the diffusion pro-
ceas, Evaporation of volatile components frm the alloy.
Diffusionporozi~Z in mono ent svm empt
Oversaturation 1 Mice with vacanoiesi Oversaturation
with vacancies which occur on the occasion 6f -reoiprooal diffusion
in solid substitute solutions. Concentration of excess vacancies in
monocomponent systems,
721M or
The fo-.mi of ddiftfursiiqo~nnre~ss~- The critical gem of diffusion
tive r7 ta,187
pore of neptive crystals . The significance of admixtures on the
Card 1/2 occasion of the forming of diffusion pores.
pk - 2286
DiffusiOn porosity in _metals and Alloys*
facts discussed In %Me
of the expejimntal
powdersi The totality A diffusion porosity Occurs in the
;u7~~c-yinaicateB the followings a place in crystalline (met&nic or
M,10 of many processes which tAk &tea (in the 0836 Of
non-metanio) systems. In all Oass$ invest'g coagulation
diffur,ion homogenization, elimination of distortions#
of lTdorooavities etc.) the oreating of diffusion Poros'ty 'a & Ub-
stagc on the way towards the occurrence of the real state Of ScPi
rim in the samPle* ty with which & very highly devOlOPOd 9y*tm
The diffusion Porossurfacea is connected is able to detemisle in a
of aiditional inner c transformations in the crystal
high degree the kinetics of Ph&3 this is one of the reasons
syettv. According to the author' a Opinion Id continue to be in-
why the creation of diffusion Porosity shou
vestigatea. (18 illustrations and 3 tables).
ASSOCIATICKI Not g-.1ven
ppy=TED BY:
Sms .1 of congress
kVAUABLE: LibrarY
Cara 2/2

(
1
,V-r,TJZ]21,p YA. ye. : Poo Pkfil-Math Sel (,Iles)
-- "';'Xp,~rfmemtaj inventigation of
"Ome Phynical Pl?oces"13 OccUrrlng In nintering and crnep Of ln~taln nyo
Khartkov 1 1958, 17 pp (Min Higher Edilc Tnw SSpj Rhartkov n1loys ".
Banyr,r State TI im A. M. Gorfk:Lv), 150 (, L nl~d`~r Of Labor pee
'ODjes (k , No 6, IT)q, lz~)

SOV/120-58-6-30/32
AUT,H0RS4rL2ZuzL'j1_ Ya. Y~_. and Obcharenko, N. N.
TITLE: Application of the Adsorption Pump in High-Temperature Metallo-
graphic Investigations (Ob ispollzovanii adsorbtsionnogo
nasosa pri vysokotemperaturnykh metallograficheskikh
issledovaniyakh)
PERIODICAL: P~oibory i tekhnika eksperimenta, 1958, Nr 6, pp ll?-118
. (USSR)
ABSTRACT: The authors employed an adsorption pump for the outgassilig
of the working chamber of a high-temperature metallographic
microscope; the pump was developed and investigated = the
Cryogenic Laboratory of the Physics Engineering Institute of
the AS M3~alnlan SSR.- It'is thought that the use
of the pump in such' investiC;a Lions is very desirable, in
of its characteristics; thus the operating region is known rc
be free from oil and mercury vapours, since the outgassinZ.is
done without employing a liquid; consequently, the pumping
velocity of the device increases with the increase of pressure
in the outgassed space, which is important at high temperatures
where various metal components can give off their occluded
gases. A microscope fitted with an adsorption pump is shown
Card 112

SOV/120-58-6-30/32
Application of the Adsorption Pump in High-Temperature Metallographic
Investigations
in Fig.l. In this, the working phamber 1 is in the form of
a cylinder having a volume of 1 litre. The pump is welded to
the bo-utom of the chamber, and is in the form of a tube 2
having a length of 300 mm, and a diameter of 30 mm. The tube
contaillB a cylindrical grid having a diameter of 12 mm. The
space between the grid and the tube is filled with grains of
activated carbon. The instrument is first evacuated by means
of a fore-vacuum pump. This pump is then switched off and the
tube of the adsorption pump is placed in a Dewar vessel con-
taining liquid nitrogen. In about five minutes, the pressure
in the instrument is reduced to 5 x 10-6 mm, Hg. The paper
contains 1 figure and 2 Soviet references.
ASSOCIATION: Nauchno-issledovatel'skiy institut khimii KhGU
(Scientific Research Institute for Chemistry of the Kharkov
State University)
SUBMITTED: December 21, 1957.
Card 2/2

GRGUZIN. Ya.Ye. Diehuzin. IA.IX.]: OVCHLMIIKOO N-H-
Xffect of "impitritieew on production of diffuse porosity. Ukr-
fiz.0mr. 3 no-5s696-698 S-0 '58. (MIRA 12:2)
1, ftcrlkovskly gosudarstyennyy universitet I nauchno-iseledovatell-
skly institut Viarlkovekogo goeudarstvennogo universiteta.
(Ionic crystals)

SOV/126-6-4-11/34
-AUTHOR: AMU-2; in, X&.Y*
TITIZ: Inventigation of Sintering of Metal Powders at Constant
Rate of Heating (Isoledoyaniye spokaniya motallichaskikh
poroshkov priP3t0YamnW * skorost-i nagreva)
PERIODICAL:Fizilia metalloy I metullovedenlye, 1958, Vol 6,
Nr 49 pp 650-656 (USSR)
ABSTRACT: 1jumorous attempts have boon made in the recent years
to derive expressions that would'aftquately describe the
process of sintering (Ref-1-5) in terms of the linear
shrialmge of the sintered, metal powders. However, the
laws postulated on the basis of assumdly isothermal
experimental curves were misleading since they did not
t" into account changes that had occurred. while the
sintered material was heated to the toot temperatuxe,
apart from the fact that some of the derived equations
contained constants which had no physical meaning.
It is well known that the diffusion coefficient Is a
Btructure-sonsitive characteristic and that the order
of its magnitude may be increased 2-4 times in the
Card 1/7 presence of lattice defects. Since in the course of

~-~OV/126- -1-1/3
Investigation of Sintering of Metal Powders at Constant, Rate ~f
Heating
heating to a given test temperature the number of
lattice deffeets is decreased, which in 4,-Iurn ctauses
V&3!iation of the diftasioa coefficient, ths results
of any investigation of a diffusion prozaas occurring
undLer isothermal experimental conditions in a material
with a distorted crystal lattice will be affected by
the rate of heating. This fact is illustratz-td *ty the
results of experiments in whiah two identical ms-10-M-L
"^0
CC .1 C
powder compacts were sinte32*d isothe--mially at ,
having attained this temperature at two different rates
of heating (F:Lg.1): It is obvious that t1he "isctherual"
exirves obtainad in these -two cases are described by
quite different kinetic equations. These conside rations
have led the present author -to belis-ie that the kinetics
of shrinkage during sintering should ba studiad
continuously in the course of the whole of the heating
cycle and since the way of varying the temparaturts, T,
with time, t, which is simplest and presents least
Card 2/7 experimental difficulty, corresponds 'to dT/d-t = const,,

SOV1126---6-*'e'-!' 1/34
Investigation of Sintering of Metal Powders at Constant Rate of
Heating
all tees in the course of the present im:9estigation.
were carried out at various constant rates of heating.
The results of the experirants in which dilatometri:~
measurements were taken on pressed, copper po'kler
(particle size - 40 g) compacts (initial porosity - -40%)
uir.tered in hydrogen at constant re.,es of hp-ati.-.g
rarLging from 5 to O-OPO/sec are reprcAuced on FiZ;.2
the form of graphs showin, the time-depondenee of ;no
relative shrinkage (AL/Lo5 of the speciwi)s. Each cf
these curves (except one r,,orrespor-d-ing to the lowest
rate of heeting) was characterised ty a dfifleactien
point. One of the poEsi-ble causes of tht!~* defleoti~~n
points might have been a decrease of bile vumter of
pores in the pressinp. Howevert since it was foiiid
that the temperature at which they o,,,curred dl-I not
depend on the initial porosity of pressings tezte"3
specially to check this point, it was zor.-I,luded that
they were caused by a decrease of the f
card 3/7 the powder particles, a property Vncse qialitatllfe

S oy/l-:; 6-6 -4-i.-L/34
Investigation of Sintering of Metal Povide:-s at Constant Rate of
Heating
me;aaure is tho self-diffusion coefficient Di, To get
a clearer picture of the laws governing the investigated
phenomena, graphs of the temperature dependence of
AL/11b (Fig.4) and d A-:~ AT (Fig-5) were constructed.
LO
The character of the relationship between the position
of' the deflectioa points and the rate of cooling, w, is
Shown clearly by the graphs on Vig-5: With decreasing
w the maximun on these curwes is shifted towards the
hf.gher temperature values. The fact 'that there io no
imiximum on the graph corresponding to w = 0.050C/see
indicates that in this case deflection point is
situated above 10000C. On the basis of the well know
equation describing the kinetics of linear shrin]mge
:La sintered powder pxessings (Eq.4) and graphs of the
temperature dependence of AL/Ijo (Fig.4), graphs of the
temperature dependence of the self-diffusion
coefficient D were also construeted. It was shown
Card 4/7 that (i) Unlike the case of undistorted crystal lattice

SOV/126- 6-4-1i/':,~4
Inveotigation of Sintering of Metal Powdsrs at ConstanV Rate of
Heating 0
for which D Ir"the effective malf-diffusion
coefficient in the crystal lattice of "active"
(eleotrolytic) povAers is not a monotonic function of
the temperatuiv. (ii) The h104r the rale of beating,
tho higher value of D is attained at any given
tomperature. (iii) With increasing w, ths maximum on
cur"s 1) = ip(T) is displaced towards the
i iv = coast.
tomperal --Is. lt has been Bhown by Pines
(Ref-596) that a basic characteristic of the processes
associated with the rtvacval of lattice dafocts consists
of a temporary excess of vacant lattice sites. Since,
according to the present views on the vacancy mechanism
of self-diffusion, the self-diffusion coefficients of
atoms, D., and vacancies, Dj~, are connected by a
relationship Da = t Db (Raf.9). where E = vacancy
concentration, it is possible that one of the principal
causes of the comparatively high values of D in
Card 5/? 'active' poviders is the fact that the actual vacancy

SOV/126-6-4-11/'-'14
Investigation of Sintering of Metal Powders at Constant Hate of
Hefttiag
concentration', is higher than the equilibrium
coacentration, o. Prompted by these considerations,
the present alor used the experimental data on the
t
ldzeticB of shrinlage during sintering to study the
degree of vacancy supersaturation of the lattice and
the kinetics of the process by which the equilibrium
concentration is attained. To this enfl, expressions
for the relative supersaturation of the lattice
(INS/ 50 =L- j 0 ) as a function of the rate of
0
heating v (BqT.9) and temperature T (Eq.10) were derived
and the appropriate graphs (Fig.7 and 8) constructed.
In agreement with the experimental results obtained by
the present author when studying the kinetics of
coalescence of excess vacancies (Ref.7), the curvus of
the temperature dependence of show that the hioar
Vie rate of heating the higher s e degTee of super-
saturation at a given temperature and that for anT given
w the relative supersaturation decreases with rising
card 6/7 t,amperature. The results of the present investigation

Sw/12ro-6-4- L 4/34
Investigation of Sintering of Metal Powders at Constant Rate of
Heating
indicate that the vacancy concentration in sintered,
eloctrolytic copper powder pressings exceeds the
egiilibrium concentration even when slow rates of heating
-he
(w = 0.05OC/See) are emplo3ed and temperatures near 44.
melting point are reached. Similar conclusions were
reached by the present author and his co-workers in
another investigation described elsewhere (Ref -3),
There are 8 figures and 10 Soviet references.
ASSOCILTION: Khar1kovskiy Gosudarstvennyy Uni-versitet
(Fharlkov State University)
SUMTTED: 26th February 1957.
Card ?/?

AUTHOR: %. Geguzin, Ya.Ye. SOV/126-6-5-10/43
TITLE: In7.restigation of Creep in Metals and Alloys (Issledovaniye
kr.ipa metallov i splavov) Part II. The Influence of Dis-
tortion Removal on the Kinetics of the Initial Stage of
Creep of Metals Having a Distorted Crystal Lattice
(11. 0 vliyanii protsessa snyatiya iskazheniy na kinetik,.~
nQchalln' ii kripa metallov' s iskazhennoy kristalliche-
skoy reshMoy'
PERIODICAL: Fizika Metallov i Metallovedeniye, 1958, Vol 6,
Nr 5, pp 825 - 831 (USSR)
4.
ABSTRACT: In the case of small loads, the kin3tics of creep can te
worked out from the speed of the cdflusion diaplaceme;:.~'Z of
atoms, as the activation energy of self-diffusion a=C --reep
coincide. Therefore, it caL be assumed that the factozs
influencing the self-diffusio.,a ;'L metals also influer_,'~O_- the
kinetics of creep. The coefficiert of self-diffusior, being
extremely stiucture sensitive, shr-~,rs up in minute clanEes
o-acurring in the crystal lattice. in the work described in
this paper, the early stages of creep in copper havi--E a
heavily distorted lattice were studied with a view to
obtaining information about the kinetics of the healing of
Cardl/? distortions. Experiments were carriei out on pla5tically

SOV/126--6--c-10/43
Investigation of Creep in Metals and Alloye. I-art II. The
Influence of Distortion Removal on the Ki.,16tics ol' the Initial Stage
of Creep of Metals Having a Distorted Crystal Lattice
deformed and electrolytic coppez.,. TAie research apparat-i3
is shown digrammatically in ~1!116ui~e -1. The heating element
consists of a quartz tube around which nichrome wire is
wound and which is covered wit~~- as'bestop. The temerature
gradient along the specimen le:4,rth is o.-.-tly about I , which
is achieved by Lneven winding and by a long copper tube
placed inside the quartz tut-3. T-',ie elonfSation of the
specimen is measured by means of -'Vhe "mirror and scale"
method. A small iron roO, the which is free
to slide up and down inside t, t~-~~t--tube, is cortrolled ty
a solenoid fixed at the bottom of the t'sst-5ube. The
specimens were plastics.). -1y--;.1.EI d 0.5 Lim wire and thin.
s,k-Prip of electrolytic cop-pe:-. -111 measi.t:-ements were
carried out in a vacuum of 10-2 to ~0-3 mmHg col. The
various loads used (0.45 to 7 kg/cm ) were all below t4he
creep limit. All experiments were carried out at a
constant heating rate. The effecti7e toughness was wo.:kedd
Card2/? ou~from the relationship:

SOV/126-6-5-10/43
Investigation of Creep in Metals and Alloys. Part II. The Ineluence
of Distortion Removal on the Kinetics of the Initial Stage of Creep
of Metals Having a Distorted Crystal Lattice
p
d _AL) W
dt Lo )
where p specific load, w - rate of heating and
AIWL0 - relative elongation. On heating a loaded spec.-Imen,
the lattice of which is distorted, the relationship
AL A 0 = (P(T) begins to deviate at a certain temperat-jxe
fxom the usual "heat course" associated with heat expansior.
Zais deviation is due to creep. The first series of
experiments is concerned with an investigation of the
extent of deviation of the elongation of the specimen from
the "heat course" and the dependen,~e of the temperature
at which this deviation commences on the degree of lattice
Card3/,? distortion. The general nature of this relationship is

SOV/126-C-r-5-10/43
Investigation of Creep in Metals and Alloys. Part II. The
Influence of Distortion Removal on the Kinetics of the Initial
Stage of Creep of Metals Having a Distorted Crystal Lattice
illustrated by strain-time curves for a powder metal-!,=Si--al
copper specimen (see Figuze 2), in which the specimen was
tested after annealing at various temperatures. The higher
the annealing temperature, the higher the temperature a-"O-
which deviation from the "heat colurse" commences on sub-
Sequent straining.. Similar ex-periments with a plastically
deformed copper specimen (see stra-in-temperat-ure curves,
3igure 3) led to the following conclusions:
.9) the elongation obtained in addition to, that due to
heating is associated with creep and is greatest for the
first heating, decreasing with increase in the number .,f
subsequent heatings;
b) the temperature at which creep becomes evident i-rczeases
with repeated heating.
Further experiments were carried out with electrolytically
deposited copper in order to study the relationship between
the degree of lattice distortion and creep. By varying the
Card4/7 current density of deposition, different degrees of lattice

SOV/126-6-5-10/43
Investigation of Creep in Metals and Alloys. Part N. The
Influence of Distortion Removal on the Kinetics of the Initial
Stage of Creep of Metals Having a Distorted Crystal Lattice
distortion are obtained, the latter increasing with
increasing current density. The results are represented
in the diagram, Figure 4, which confirm the fact that the
9-reater the distortions of the lattice the lower the
temperature at which creep commences and the greater the
degree of elongation. Electrolytically produced specimens
fail in high-temperature creep tests by intercrystalline
fracture. This is due to formation of vacancies which
reduce the cross-sectional area of the specimen. The
object of this second series of experiments was to study
the influence of the heating rate of deformed specimens on
elongation due to diffusion creep. The results obtained
are given graphically in Figure ~ in which the curves show
that the relative elongation increases with decrease in
heating rate. From Figure 6,,in which the effective
toughness is plotted against temperature, it can be seen
that as the heating rate up to a certain definite tempera-
ture is increased, so the yield strength at that temperature
Card5/7 increases. The curves obtained for the kinetics of stepwise

SOV/126-6-5-10/43
Investigation of Creep in Metals and Alloys. Part II. The
Influence of Distortion Removal on the Kinetics of the initial
Stage of Croep of Metals Having a Distorted Crystal Lattice
heating with an isothermal soaking time at each step of
20 min (Figure ) are similar to tl,.ose described by Pines
et al (Figure 3~. Besides$ X-ray photographs were taken
of deformed and electrolytic copper specimens in order to
study the relation between rec::-Istallisation and heating
temperature (Figure 8). By comparing these X-ray photo-
graphs with the creep curves, it is possible to conclude
that the collective tecryEtallisation taking place in a
deformed specimen during heating does not fully remove the
ce.use responsible for the increase in creep rate. This
cause may be a network of cracks (Ref 12) present in
electrolytic metal, or develoD~.ng in e.eformeC metal. As
the grains coarsen, the microcracks in the lattice may be
preserved and may cause an increased creep rate at tempwa-
tures at which growth of recrystallised grains becomes
evident.
There are 8 figures and 12 references, 11 of which are
Card6/7 Soviet and I English.

SOV/126-6-5-10/43
Investigation of Creep in Metals and Alloys. Part 11. The
Influence of Distortion Removal on the Kinetics of the Initial
Stage of Creep of Metals Having a Distorted Crystal Lattice
ASSOCIATION: Kharlkovskiy gosudarstvenngy universitet imeni
A.M. Gorlko 0 (Khar'kov State University imeni
A.M. Goeklyr
SUBMITTED: February 25, 1957
Card 7/7

SOV/137-59-5-10207
~-ransiation from: Referativnyy zhurnal, Metallurglya, 1959, Nr 5, p 107 (USSR)
Ye,
AUTHOR! _~6
TITLE- On ~.he Phenom4non of' "Growth" in Sintering lntersolubl.e Metal
Powdsrs \$
PERIODTCAL, Uch. *zap. Khar1kovsk. un-t, 1958, Vol. 98, TT. Fiz. otd. f1z,-
matem. fak., Vol 7, pp 267 - 273
ABSTPk~T- Experimental Investigations were carried out into the temporary
dependence of the magnitude of linear thrinkage in sinterIng
pressed products of CuA.!Li-i(niders and their " mixtures. Re-
sults of measurements were used to ceaculate the magnitude of
"growth" on an A - B type contact. The dependence of this va-lup
on the initial porosity of the pressed products is shown, The
presence of Ointernal" free vollume In the porous pressed product.
caused reduced "growth', which was dilatometrically measured. Tns~-
author analyzed Ithe Problem on the possible Inhibition of the
"growth" by a mixture of interd-Iffusing metal powd,~rs.
Card 1/1 1 B~

AUTHOR: Geguzin, Ya. Ye.
SOY/2o-12o-4-36/67
TITLE: On the Activation Energy of the Diffusion Creep of Metallic
Disordered Solid Substitute-Solutions (0b energii aktivatsii
protseesa diffuzionnoy polzuchesti metallicheskikh neuporya-
dochennykh tverdykh rastvorov zameshcheniya)
PERIODICA,L: Doklady Akademii nauk SSSR, 1958, Vol. 12o, Nr 4,
pp. 819 - 822 (USSR)
ABSTRACT: The experimental data on the irreversible deformation of metals
at high temperatures and stresses (if the velocity of extension
is proportional to stress, j- P) can quite satisfactorily be
explained by the mechanism of diffusion. These conceptions base
upon the following idea: The macroscopically observed flow is
the consequence of a directed stream of vacancies which is due
to autodiffusion. This stream forms under the influence of the
gradient of the concentration ' of vacancies. There are 3 inde-
pendent methods of determining the activation energy of the
diffusion creep of disordered solid substitute solutions: a)
From the data on the temperature dependence of the coefficients
of the autodiffusion of the solution components in a solution
Card 1/3 of given concentration. b) From the heat of fusion of the

On the Activation Energy of the Diffusion Creep of SOY/2o-120-4-36/67
Metallic Disordered Solid Substitute-Solutions
component + f the solution, and from the difference
U0 - U I -U II , which is determined from the diagram of
0 0 1 11
equilibria. u0 reap, u0 denote the energy of mixing per
particle in the liquid and solid phase respectively. c) By
experiment from the temperature dependence of the velocity
of the diffusion creep of the disordered solid substitute-
solutions of given concentration. These 3 methods can be verified
on the basis of the example of the system Au - Ni. The
verification of the methods a) and b) is discussed in short.
Both methods lead to the same results. The authors also carried
out creep experiments with samples of the alloy Au - Ni (50 -
50 atom per cent) at 800, 860 and 9200. The activation energy
of the diffusion creep was found to be (45� 2).10 cal/mol.
This experimental value agrees satisfactorily with the theoret-
ically computed ones. The authors finally give the theoretical
and experimental values of the activation energy of the
diffusion creep for the aystems Cu - Ni and Pb - Sn. There are
Card 2/3 1 fiRure, i table, and 15 references, 11 of which are Soviet.

Onthe Activa-tion Energy of the Diffusion Creep of SOY/2o-120-4-36/67
Metallic Disordered Solid Substitute-Solutions
ASSOCIATION: Kharlkovskiy gosudarstvennyy universitet im. A. M. Gorlkogo
(Kharlkov State University imeni A. M.,Gor1kiy)
PRESENTED: January 15, 1958, by G.V.Kurdyumov, Member, Academy of
Sciences, USSH
SUBMITTE*;): January 10, 1958
1. Metals-Deformation 2. Metals--Creep
4. Diffusion--Theory 5. Mathematics
3. Metals--Stresses
Card 3/3

24(0)
SOV/25-59-2-4/48
AUTHOR: Ges~zin Ya-Ye - Candidate of Physico-Mathe-
matical. Sciences (Kharkov)
TITLE: An Important Problem (Vazhnaya Problema)
PERIODICAL: Nauka i zhizn', 1959, Nr 2, p 11 (USSR)
ABSTRACT: The article concerns the Vsesoyuznoye nauch-
noye soveshchaniye po voprosam fiziki proch-
nosti (All-Union Scientific Conference on
Problems of the Physics of Solid Bodies),
held at the Kharlkov State University from
26 to 28 Nov 1958. The conference was at-
tended by more than 200 scientists and en-
gineers of Moscow, Leningrad, Sverdlovsk,
Kiyev, Khar1kov, Kuybyshev and other Soviet
cities. The academician G.V~Xurdryumov,
who opened the conference, drew the atten-
tion of the audience to the fact that the
roblem of the physics of solid bodies
Card 1,12 Keglected during the post-war years), is

SOV/25-59-2-4/48
kn Important Problem
now the focus of interest of many scienti-
fic research institutes. This interest is
explained by the new tasks arising in con-
nection with the development of atomic en-
gineering, space flights and the urgent need
for materials which are highly stable within
a wide range of temperature. One of the most
interesting problems discussed at the con-
ference was the problem of stability of solid
bodies under pressure, A number of reports
were dedicated to this problem, which clearly
indicated that microscopic flaws in the solid
body considerably reduce its stability and
that the "lifetime" of the obj,-,ct under pres-
sure'is also reduced by an increase of tCMDera-
ture. On the whole., 45 reports were delivered
at this conference, which was attended by a
Card 2/2 large number of young physicists.

SOV/70-4-4-18/34
AUTHORS: Geguzin, Ya.Ye. and Shpunt, A.A.
TITLE: The Investigation of the Process of High-temperature
Self-healing of Macro-defects on the Surfaces of Single
Crystals of Rock Salt
PERIODICAL: Kristallografiya, 1959, Vol 4, Nr 4, pp 579-586 (USSR)
ABSTRACT: Details of the levelling of the surface of a single
crystal of NaCl which occurs at high temperatures (up to
790 0C) have been observed and described. Using micro-
scopic and interferometric methods the healing of
artificially produced defects in the form of gr~ooves of
definite geometry has been observed. It is showiLthat
the process of self-healing of grooves proceeds with a
speed diminishing with time. It in found that the dis-
tortion of the crystal lattice promotes the acceleration
of the process of the high-temperature healing of the
defect. It in further shown that transport of material
in the gaseous phase substantially determines the kinetics
of the high-temperature healing of macroscopic surface
defects.
Cardl/2 The grooves were made with a diamond pyramid from a m 'icro-
hardness tester. The angle between opposite faces was
-n-

SOV/70-4-4-18/34
The Investigation of the Process of High-temperature Self-healing
.of Macro-defects on the Surfaces of Single Crystals of Rock Salt
1360 and various lcols were used. Material from the groove
was displaced ixLto a ridge either side of it and a
calculation of the energy in the groove is made. The
contours of the grooves were plotted at intervals with
an interferometer. Acknowledgments are made to
V.I. Startsev. There are 9 figures and 8 references, of
which 6 are Soviet and 1 German, 1 English.
ASSOCIATION: Vsesoyuznyy nauchno-issledovatellskiy institut
Ichimichoskikh reaktivoy "IREA" Khar1kovskiy filial
(All-Union Scientific Research Institute for Chemical
Reagents "IREA", Khar1kov Branch~
SUBMITTED: October 3, 1958
Card 2/2

AUTHOR: Goguzin, Ya.Ye. SUV/126-7-1-10/28
TITLE: Investigation of Creep of Metals and Alloys (Isaledoyaniye
kripa metallov 1. splavoy) III. The Effect of the Specific
Lead on the Kinetics of the Initial Stage of Creep in Metals
With a Defective Crystal Lattice (111. 0 vliyanii velichiny
ud.ellnoy nagruzki na kinetiku nachallnoy stadii kripa
metallov s iskazhennoy kristallicheskoy reshetkoy)
PERIODICAL: Fizika Metallov I Metallovedeniye, 1959, Vol 7, Nr 1,
pp 72-78 (USSR)
ABSTRACT: The experiments were earried out using the apparatus and
technique des.,ribed earlier by the author (Ref.3). In the
first series of tests the author studied diffusion creep of
copper samples with defective crystal lattice, to which he
applied different loads, On beating at the rate of 5OG/min
diffusion creep of identical plastically deformed copper
samples was studied under loads of 3.25 and 5.75 kg/eM2.
The results obtained are shown in the form of temperature
dependence.of the extansion per unit load (Fig.1) and
Card 1/3 viscosity (Fig.2). Similar experiments were made on copper

Investigation of Creep of Metals and Alloys III. The Effect of the
Specific Load on the Kinetics of the Initial Stage of Creep in Metals
With a Defective Crystal Lattice
sExples of electrolytic origin. The results are shown in
Figs.3 and 4s Figure 3 gives the time dependence of the
extension per unit load, and Fig.4 shows the extension, and
the extension per unit load as a function of the applied load.
In the second series of tests the author studied diffusion
oreep both under the conditions of -uniform rise of temperature
and when temperature was hald constant for long periods. The
results for plastically deformed coppe.- samples are shown in
Fig.5 In the forsi of dependenv,e of extension on time. Figs.
6 and 7 show the time'dependenog of the extension per unit
load for copper samples of electrolytic origin. The results
obtained show that small loads, below the elastic limit,
produce healing of defects similar to healing produced by an
increase of temperature. This effect is due to a tranaZzmatim
of dislocations, under an applied external load, to dislocations
of the type which are more easily healed by thermal fluctua-
tions. Acknowledgments are made to I.M. Lifshits and
h1.1. XaganOT for their advice. There are b figures and
Card 2/3 8 referenees, of which 5 are Soviet and 3 English.

Investigation of Creep of Metals
Specific Load on the Kinetics of
With a Defective Crystal Lattice
SUV/126-7-1-10/28
and Alloys III. The Effect of the
the Initial Stage of Creep in Metals
ASSOCIATION: Khartkovski-y gosudarstvennyy universitet imeni A.M.
Gor1kogo (Kharikoy State University imeni A.M. Gorlkiy)
SU13MITTED: March 18, 1957
Card 3/3

24(6) 18(7)
AUTHOAS:._Geguzin, Ya. Ye. and
TITLE: Investigation of the
(Issledovaniye kripa
4. Creep of Lead-Base
svintsovoy osnove)
Kudrik, V. I.
SOV/126-7-2-11/39
Creep of Metals and Alloys
metallov i splavov).
Alloys (Krip splavov na
PERIODICAL: Fizika, Metallov i Metallovedeniye, 1959, Vol 7, Nr 2,
pp 235-242 (USSR)
ABSTRACT: The experimental apparatus used in this work differed
from the one described earlier (Ref 3) only by the fact
that suspension devices were provided for two threads
and with them two independent drums with mirrors. This
enabled the kinetics of creep of two specimens to be
observed simultaneously under identical conditions. Two
specimens of the same alloy were installed in the
apparatus, one specimen was thoroughly annealed and the
other plastically deformed. Metals of 'lie following
purity were used as basic iniaterials: 11b - 99.994%;
Sn - 99.98%; Cd - 99.94%; Sb - 99.90%. The threads were
obtained by extruding the alloys through a steel die of
0.5 mm dia. Prior to testing the threads were given a
Card 116 homogenizing anneal for two hours (above the testing

SOV/126-7-2-11/39
Investigation of the Creep of Metals arid Alloys
temperature). The formation of the threads of 0.5 mm
dia. was carried out by pressing them into ribbons of
0.1 mm thickness between two polished steel plates. The
test was carried out as follows: Up to the teaperature of
isothermal soaking, the specimens were heated at a
constant rate 5 C/min, after vhich they were isothermally
soaked ior 3.5-4 hours. A specific load of approximately
3 kg/cm was applied to the specimens in the experiments,
i.e. a load which is considerably lower than the elastic
limit of the alloys in the temperature ran6e at which the
tests were carried out (Ref 4). In order to be able to
Calculate correctly the temperature behaviour (elongation
as a result of thermal expansion on heating) from the
curve within the coordinates (A L/L )-t, experiments for
the determination of the relationship between
concentration and the coefficient of linear expansion
were carried out for all investigated alloys, using
nassive Q mui dia) thoroughly annealed specimens. As
shown in the calculation, the relative error in the
Card 2/6 determination of the viscosity -q was 3.5%. All the

SOV/126-7-2-11/39
Investigation of the Creep of Metals and Alloys
experiments were carried out in a vacuum of 10-2 to 10-3mm
F(g col. The following alloys were investigated:
The Pb-Cd system Pb + 1 at.% Cd; Pb + 3.5 at% Cd;
Pb + 2 at.% Cd; Pb + 5 at.% Cd;
Pb-Sn it Pb + 5 at.% Sn; Pb + 20 at.% Sn;
Pb +1D at.% Sn; Pb + 25 at.% Sn;
Pb-Sb to Pb + 1 at.% Sb; Pb + 3.5 at.% Sb;
Pb + 2 at.% Sb; Pb + 5 at.% Sb.
From each experiment two curves were obtained which
d~escribed the behaviour of a deformed and an undeformed
Specimen. On each of these curves there was one
portion which corresponded to the heating period and
one corresponding to isothermal soaking. In Figs 112
and 3 typical experimental curves are shown which were
obtained in experiments with alloys belon6inG to various
iiyatomn. In those fiL7,ures tho curves I refor to
undeformed and curves II to deformed specimens. The
curves obtained were also used for determination of the
dimension of the scale and the ma,~ni7:;ude of elongation
Card 3/6 due to creep associated with deformation. -C."urve III

--.OV/126-7-2-11/39
Investigation of the Creep of Metals and Alloys
(Fign 1,2 and 3), which describes this contribution,
has been obtained by graphic deduction fro;-,i curves I and
II. In Fig 4 the dependence of the toughness of a
13 ecimen in equilibrium, a) on the true concentration and
on the relative concentration is shown. In Fig 5 the
1
dependence of the toughness of a deformed specimen on
the relative corleentration is shown. In Fig 6 the
dependence of Zj on the relative concentraLion is shown.
In Fig 7 the relaltiogship AL/L9 = (P(t) for a Pb(80%)-
Sn(20%) alloy a8 180 C is shown. 1 undeformed specimen
annealed at 185 g for two hours; 2 after supplementary
annealing at 1850C for 5.5 hours; 3 after supplementary
annealing at 190 C for one hour, In Fig 8 curves for the
dependence of tH on the relative concentration of the
solid solution are shown. In Fig 9 curves for the
dependence of tR on the true concentration of the solid
Card 4/6 solution are shown, In Fig 10 the dependence of 6 H on the

SOV/126-7-2-11/39
Investigation of the Creep of Metals and Alloys
true concentration of the solid solution is shown.
As a result of their experiments, the authors have
arrived at the following conclusions:
1. As the alloy element content of the solid solution
increases, its deformation occurring during creep
is facilitated, i.e. the effective toughness decreases
whereas plastic deformation becomes more difficult.
2. From the investigated alloys it has been found
that the rate of creep of the solid solution alloy, the
lattice of which is in equilibrium or in quasi-
equilibrium, is determined not by the true concentration
of the alloy elements but by the degree of saturation
of the solid solution.
3. The results of creep experiments with plastically
deformed specimens are discussed on the basis of the
theory of exhaustion, which occurs during dislocation
creep. It has been found that, for the same degree of
deformation, dislocation regions with a lower
activation energy for the healing process appear in the
Card 5/6 Investigated solutions as the concentration of the

ISUV/126-7-2-11/39
Investigation of the Creep of Metals and Alloys
solvent element increases.
lbere are 10 fiSures and 8 references, 5 of which are
cioviet, 3 English.
ASSOCIATION: KhaAovskiy gosudarstvennyy universitet imeni
It. M. Gor:kogo (Kharlkov State University imeni
it. M. Gor kiy)
SUBMITTED: June 19, 1957
Card 6/6

67713
SM/126-7-3-9/44
AUTHORS: Goguzin,,_Ya. Ye. and Vishnovskiy_,_I. I.
TITLE: Investigation of of Metals and Alloys. 5. (laaledov-
anlys krips. metallov I splayov. 5.) Early Stage of Creep
in Plastically Deformed Filaments of LV_1-�A5,1Alloy
(Roinnyaya stadiya krips. plastioheaki deformirovannykh
nitey splava Pb--Su)*,\
n:tallovedenlye,
PERIODICAL: Fizlks metallov I
Vol 7, Nr 3, pp 367-
371 (USSR) - t~41
ABSTRACTi The present work was carried out with the aim of accurately
checking the Interrelation between the kinetics of healing
of' distortions and the kinetics of the initial stage of creep
ir. three substitutional solid solutions. The object for in-
veatigation was a solution of tin (25 at.,%) and lead (75 at4).
Such a concentration of tin is close to the limiting concen-
tration of the *-solutloft at euteotio temperature, and hence
it can be expected (Ref.2) that all effects associated with
the influence of deformation on creep will be shown very
clearly. The same method for making the specimens and
carrying out measurements was used as by Geguzin et alia
Card 1/49 (Rof.2). Two aeries of experiments were carried out.

67713
SOV/:L26-?-3-9/44
Investigation of Creep of Metals and Alloys. 5. Early Stage of
Creep in Plastically Deformed Filaments of Pb--Sn Alloy.
The experiments of the first series wore carried out with
the aim of finding the influence of the extent of Initial
distortion of the crystalline lattice of the solid solution
on the kinetics of the early creep stage. The specimen
WA3 first plastically deformed. The experiments were
ca:rried out at a constant heating rate (Rof .3) ( w - 70/min).
As can be.seen from Fig.1 the healing of a portion of Z-19
distortions taking place on heating causes creep to not In
at higher temperatures and leads to smaller elongations of
the specimen. The specimens were prepared as follows.
Filaments of the alloy, obtained by drawing throug4 a steel
die of 0.3 mm diameter, were thoroughly annealed at 1900r
for two hours, after which they were compressed to different
dogrees between polished steel plates. Measurements were
carried out on specimens having the shape of strip of
thieknessest 0,18 am (Ld = 0.12 mm); 0.13 mm (iNd = 0.17 zW
and 0.09 mm ( Ad = 0.21 mm). The elongation was studied,
Card 2/6 both at constant heating rate wil = 50/min (Fig.2) and

,;J~713
126-7-3-911V~
Investigation of Creep of Metals and Alloys. 5. Early Stage of
Creep in Plastically Deformed Filaments of Pb--Sn Alloy.
I
were carried out at a specific load of
Rud = 6.2 kk1cM
In Fig;4 the time dependence of AL/LoRud during continuous
creep of the specimens with different initial crystal lattice
distortion is shown. Experiments of the second series
were carried out with the aim of studying the kinetics of
creep of specimens having the same lattice distortion, loaded
at different rates. The heating rate was varied within the
lizLits 0.35 - 3WOO/min. In Fig.5 the relationship
AL/LoRud = f(T) of equally deformed specimens on heating
at a constant rate is shown. The phenomena determining
tho nature of the curves in Fig.6 can be conveniently
discussed by considering the dependence of the effective
yield strength of the investigated specimens on temperature
at constant heating rate, This rolatignship was determined
from curves shown in FJLg.5 with the help of the relationship
(Ref.3)
X d ( AL
Card 3/6 dT LoRud
ants
in Isothermal treatment at 1800C (Fig.3). All exper

67713
SOV/126-7-3-9/44
Investigation of Creep of Metals and Alloys. 5. Early Stage of
Creep in Plastically Deformed Filaments of Pb--Sn Alloy.
The value of _S !, LL '. Is found graphically by
dt ~ LoRud )
differentiating these curves. The dependence of z On T
is expressed In the form of graphs ln j: = Y (T) In Fig.6.
An a result of the above investigations the authors have
arrived at the following conclusions:-
(1) The kinetics of creep of a solid so;,ution depends
essentially on the degree of distortion0of the crystal
lattice cf'th* specimen.
(2) The creep of a specimen with distorted lattice under
Isothermal experimental conditions is accompanied by
hauling of the distortions. In specimens with a given
delgree of Initial lattice distortion the healing process
in accomplished the later and the quasi equilibrium
condition setting In Is the further removed from equilibrium,
the greater the Initial deformation of the specimen.
Card 4/6

O'l I
SOV/126-?-3-9/44
A caireef or metals and Alloys. 5. Early Stage of
vestijaplo t;ff
Mop an ly 4rormed Filaments of Pb--Sn Alloy.
(3) N.Veriments in which creep of speeimens with a distorted
oryistal lattlo% at various heating rates, was Investigated
havo shown that the kinetics of distortion-removal from a
soUd solution is qualitatively analogous to the one observed
earlier in distorted metallio powders (Ref.3. 4). The
particular characiteri8tio of this kinetics consists In the
fact that'the effective kinetie coefficient (in this case
the effective coefficient of yield strength) in not a
constanit'funation of temperature. The non-coistant nature
of the dependence of the effective kinetic coefficient on
temperatupe may be the result of the fact that the creep of
an alloy in determined by essentially different mechanisms
in various temperature ranges: by a dislooation mechanism
at low temperatures and by a diffusion mechanism in a
temperature range at which healing of dislocated regions is
essentially accomplished.
Theirs, are 6 figures and 6 references, of which 4 are Soviet
Caxd 5/6 atWI 2 English.

sov/i26-7-4-12/26
AUTHOR: Gejnj!~ ~n,~..Ye.
TITLE: Investigation of Creep of Metals and Alloys.
6. Diffusion Creep of Binary Substitutional Solid Solutions
PERIODICAL: Fizika metallov i metallovedeniye, 1959, Vol 7. Nr 4,
P11 572-585 (USSR)
ABSTRACT: According to the contemporary views on the mechanism
of diffusion creep of crystalline substances (Ref 1,20,
5.) the change of the shape of a body in creep is
dt9termined essentially by the coefficient of self-
dIffusion of the vacant lattice sites and, in the case
o:r pure metals, this has been confirmed experimentally
CRef 5,6,7sl2). The theory of diffusion creep has been
formulated for pure metals. i.e. for single-phase
crystalline systems consisting of atoms of one element
and lattice vacancies and it was the aim of the present
author to apply these concepts to disordered solid
substitutional solutions, i.e. to single-phase,
2-component, crystalline systems consisting of two
types of atoms and lattice vacancies. In his attempt to
interpret the obtained experimental data on the
Card 1/12 temperature dependence of diffusion viscosity of the

SOV/126-7-4-12/26
Investigation of Creep of Metals and Alloys. 6. Diffusion Creep
of Binary Substitutional Solid Solutions
solutions, the author assumed that tile deformation
in creep, in this case is associated (like in pure
metals) with a continuous flowaf vacancies, and that
the gradient of the vacancy concentration by which this
flow is determined is a result of tile action of
externally applied load. To determine whether, and to
what extent, tile creel) characteristics are relnted to
the type of the equilibrium diagram of the metallic
system (or rather to the physical constants determining
the form of the equilibrium diagram), the author studied
experimentally the concentration and temperature
dopendence of the diffusion viscosity of three systems:
copper - nickel (complete solid solubility);
gold - nickel (the same as before but with a minimum on
tile liquidus and solidus curves) and lead - tin (partial
solid solubility with an eutectic). In tile first part of
his work, the author derives semi-empirical expressions
for the concentration and temperature dependence of the
viscosity coefficient of a solid solution. He starts by
Card 2,12 pointing out that change of entropy, AS, on melting is the

Sov/i26-7-4-12/26
Investigation of Creep of Metals and Alloys. 6. Diffusion Creep
of Binary Substitutional Solid Solutions
same for all metals and substitutional solid solutions
and that it is independent from concentration (Ref 8 and
9). Taking into account the latter fact, he then
introduces a concept of fictitious" melting point of an
alloy constituting a substitutional solid solution.
This magnitude can be determined from Eq (1) from which
Eq (2) is obtained. In these expressions T.W -
"fictitious" melting point of the solution; c - its
concentration; Ts(O) - melting point of the solvent
metali Q(O) the latent heat of fusion of the solvent
metal; Qk(c) "configuration'? heat of fusion of the
solution with concentration c; AS - change of entropy
on melting of the solvent metal. By using the known
~Ref 18) formula for Qk, an expression is derived
,(Equation 3) for the concentration dependence of Ts(c),
in which Ul and ull are the displacement energies in
0 0
liquid and solid phases, respectively; QA and QB - latent
heats of melting of pure metals A and B; N - number of
particles. After drawing attention to the fact that the
Card 3/12 produce y JDb CI concentration of vacant lattice

SOV/126-7-4-12/26
Investigation of Creep of Metals and Alloys. 6. Diffusion Creep
of Binary Substitutional Solid Solutions
sites) at temperature corresponding to the "fictitious"
melting point does not depend on the concentration of the
solid substitutional solution and is determined only by
the type of the crystal structure, the author points
out that the activation energy of the process of viscous
flow, 0, and the "fictitious" melting point, TS, of a
disordered solid solution are related in the same way
as in the case of pure metals, i.e. according to Eq (4),
which in combination with Eq (3) becomes Eq (5). As to
the relationship between the partial coefficients of
self-diffusion, Ds(c),and DO(c), of the components of a
binary disorderedAsolution, and the coefficient of self-
diffusion of vacancies, DC, it is described by Eq (6).
where 0 and c are the concentrations of vacancies and
eitoms of component B, respectively. The concentration
dependence of the calculated values of y(c) =Spbs(c) for
the gold-nickel system at 800, 850, 900 and 9500C is
illustrated in Fig 1. Curves reproduced in Fig 1 were
used for plotting graphs of the relationship Iny versus
(1/T - 1/T8), where Ts(c) - the "fictitious" melting
Card 4/12 point at a given concentration. The values of y(c) for

SOV/126-7-4-12/26
Investigation. of Creep of Metals and Alloys. 6. Diffusion Creep
of binary Substitutional Solid Solutions
Card 5/12
tiome gold-nickel alloys at their "fictitious" melting
points, calculated from these graphs, are given in
,rable 1. Those data confirm that y(c) at T = Ts is
-practically independent from concentration. The
'validity of Eq (5) can be checked also with the aid
of data on self-diffusion in the Sold-nickel system.
on the assumption that, in analogy to pure metals,
diffusion creep in disordered solid solutions can be
described as a continuous flow of vacancies, the
magnitude JDC in the formula describing the relation-
ship between the viscosity coefficient and the
coefficient of self-diffusion of vacancies (Eq 7) can be
substituted from Eq (6) so that Eq (8) is obtained.
(In Eq (7) and (8), 6 - lattice parameter; R, L -
the characteristic linear dimensions of the testpiece.)
Since the viscosity coefficient and activation energy
are related by Eq (9) it is possible to find 0 (c)
from the slops of the straight lines in coordinates
In DIa + DA(1 - c) - I The concentration dependence
T T

SOV/126-7-4-12/26
Investigation of Creep of Metals and Alloys. 6. Diffusion Creep
of Binary Substitutional Solid Solutions
of 0(c) determined in this way is shown in Fig 2
(continuous curve representing the results of
calculation according to Eq (8) and (9); broken curve
representing the results of calculations with the aid
of Eq (53 The curve in Fig 2 can be compared with the
data obtained from Eq(5) by studying the magnitude of
deviation of the curve 9 = 0(c) from the straight line
connecting the values of the activation energy of the
viscous flow of the components of the solution.
According to Eq (5), this magnitude is determined by
the relationship
L(c) = 2OR N(ul - ull)c(l - c)
S 0 0
The concentration dependence L(c) obtained by graphical
method from curve G(c) in the form of a straight line
which corresponds to the additivity law, and the curve
L(c) calculated from Eq (5), arc shown in Fig 2. For
plotting the curve L(c) the following values were taken
Card 6/12 for the magnitudes appearing in the Equation:

SO.V/126-7-4-12/26
Investigation of Creep of Metals and Alloys. 6. Diffusion Creep
of Binary Substitutional Solid Solutions
,41S - 2.3 cal/gOC; Au = 1.2 x 10- l3erg/particle.
Comparison of the theoretical and experimental curves
L(c) indicates that the relationship described by
Bq (5) holds for the solid Au-Ni solution. Taking this
into consideration, it is possible to obtain an
expression which describes the concentration dependence
of the diffusion coefficient during diffusion creep in
binary solid solutions. From Eq (7), (9) and (3) and
taking into account the independence of the magnitude
jDs from concentration (at T = TS), Eq (10) is obtained.
b
The formulae for 0 and a appearing in this equation are
given immediately below it. Finally it is shown that
the effect of an alloying addition on the variation of
resistance of the solution to diffusion creep depends
on the concentration of the solution. In this sense
the effect of the alloying addition can be characterised
by the coefficient of hardening X(c) determined by
Eq (15), or Eq (16) derived from Eq (15) and (10). In
the second part of the present paper, the results of the
Card 7/12 experimental work are reported. The creep testu were