SCIENTIFIC ABSTRACT FR:ODING, I.A. TO:ODING, I.A.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001237800041-6
• Release Decision: RIF
• Original Classification: U
• Document Creation Date: November 2, 2016
• Sequence Number: 41
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTR

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~~ l~or t~ e ~' ~, t{ ~' -,~-e l3 ~,~ oft 9 .~
~,~, y11 ~ oyed,erii 1�...~.'~ Mort ti-' Cia~'r C , l~fl'r trengt.hening :increased at first ~-
and the2i dro,,ed a (at Ooh and 1a0,~ deforr.;atian)
I i ppxcciably (at dogeoeS of deformation of
~~ ZC�~)o A ct~an�e a.n the an~~ealin,c, temperature will also
reduce t7e effect of strengthening� The optimum for this alto
is a cleforniation of p~ 3 to 1 ~ 0~ at 600 �C, The inc~:�eas e in y
strength is attributed to the formation of Oottrell clouds
There are 2 figures and 12 references 3 Sc>vi.et-bloc and
9 nan~Saviet~�bloc~ T;ne four latest English-~�lanuuage references
r:~entioned in the text ar�~
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3(1~~~
~/zoo/G1/ooo/oo5/ago/o~.~3
Zncreasin;; the ~ ~ ~, .. EU73~E335
speci.men~ were strb~jecteci to :~t~znciard Gxc~ep torts� T}2e creep
rate dre~reased by a factor eded T}ie authors of tii:is~ pas7r.,r
aic;~ed at studyi.xi~; tn~p possibility of :iiicr~aas ~.n~ t;he long-run
str. Pn~;tki off' steel by prociucin;; poly~anaX. stri.~c:tures by
raeclianic al.-heat treatment /E335
I.11 ~ o
A., a~:id Fr~.dm~~n., Z~,G� (I~~osca~w)
Odin~~, I� --- a17.oys by 4;.he
AUTH ORS c ~.: _ ,,._...._---- __`.-....--- resistance o f
Increasing tl~.e heat-
TIT~F tiiad of mechani�al"i~cat treatment
me r~vcsti.yaJ Otdeleniye
nauk SSSR~ i toPlivo~
PERZOO~CAL~ Al~.adecuiya ~ietallurgiya
t ekhnich eskilch nau1~ u ~ ??
61 , PP � 75 of metals
nog 5 ~ 19 strenb,thenin~
roni~ation :~s Particularly
TEXT, Of the Iinawn r~echaa~~~~s o dislocations
~~ olastic deformation-, P lu T On tlic: role of
during, ~ Ref o E~rimentally the
~~5~ Ivanova (~ 6) has shown exp- ~riate
i.mpcrtant ~ n vo AN SSSR, 195 creep by G-n approi
in creep" 7~d._. ~- the speed of
of r rducin,:; ,and of gust en~:tic steels
possibility 1 Ong mechan~.cal~ i
l,~etliod of paly~yc~~:ii~ata.on of Iran
~c~na1 str�'uctures by aPP ~� dQforrnation
Ivanava c~btaine~l clurin~ creep tasty a ~'e~idua.l
t treatment ~ some critical value Anantainpd~at
lies zJhicn equal-led the lead and may.
was obtained was relieved of result of which
that the specimen 2~ Hours , as a that ~, the
the test temperature for in tl~e itietal~ Fo11a~a~in~
Polygoni~,atian cteve~-abed
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li4. /~J ~~/7 1
6 Y�
r. S/129/611000/o01/oal/o13
8111/815
Poly~on~, ~a tion in Metals
t~
authors c�nclud~.ng that subs~.;antial improvements axe oss
p ibleo
:d
Fig.B
I There ara $ figuxes and~~6 rei'erenaess 8 Soviet end 48 n
ASSOClATIONs I~rstitut metallurgic AN SS3R on"Soviet.
. (Institute of Metal~.urgy, AS US3l~~
' Card 4/~t
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~: s; ~~9E61,~o00/001/001/013
Polygonizat:~on in A~etals
F ' f
found to be facilitated b increasi
s tsucture in ferritA rain F s~ purity (~ig.7 shows polygonal ' ~,.
` g ~ ) . ig ~ and ~ (both quoted i'rom
Nochendorfex and ~w@rtz~ Archiv Eisenhiittenw@sen~, vo~.3o, No.7,
1959) show the temperature-deformation-grain area-grain-number
i
{ relations. The rate of ~aolygonization is determined by dislocation
effects which are themselves subject to various influences
(Ref,34). Polygonization occurs in cree (e.g. Refs 13-15, 35-37?
E and this effect has been studied (Refs. 3~-~.9) ~ it being shown
(Ref.2~) that with a suitable method of of
~ austenitic steels, creep rate can be greatlygreduced.n o~iiron and
shows the creep curves for Armco iron, v = 8.5 kg/mm2, T ~g450 oC: ;~~~
~ (curve 1 -normalised state, v = l .l, 14-4 D/h; curve 2 -load
relieved and ~''urnace switched of~; curve 3 -after ~~echanical t` ~
' working combined with heat tree tr~ent, v
~ 5~1a-5~,Ih~ .
~ The authors discuss such methods. Pol~gonization i;n metals
subjected to deformation and heat treatment and during crystallize- ( ~~.~
~ tion is also considered. The survey eone~.udcs with ~~ section on ~
the influence of polygonization on mechanica]. praper~ties, the
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~111./S13 5
Polygonixation,in Metals
The authors consider the intexaction of two parallel dislooations ~=~~~
(Fig.3) and. then that of many such dislocations Prom the asp�et ~~
~~~}~ polygonization. They then di$cuss polygonizatian in extension.
The distortion of sli lines in extension of a crystal is shown
' j schematically in Fig.. Mere temperature plays a mayor part.
Polygonizati~n in metals with various de tees of ` ;~~
r ~ ~ g purity has been
3 ) P1 . . 1 ~ ._.... ... ~ � j
~~'......,.. A ..,. A -.~.
z - ~~ Fig. ?i .-~....-~ , , ~ ;
. ~ ~ al
q~ '
E
i l
~~ i
... ~,
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s/x.29/6~'c~oo/oar./~3o~./a13
`~ ~~�l~.l~13 ~ ~
~~ ACTTHO~t~ s , ,
~' t ~ I.A. , Corre,~ponding ~�mber ~ Ate USSFC,
E ~ u , . ~ . , ~ngineea~, and Fric~aan 4 ~. d ~ y Rngina ~~
fi -ti
TIT~F~s :, Polyganization i~~ A~etals k'~
3 P~RI4D3 ,~L s Me tallovedeni a ~, term
~ Y icheskaya obrabotka metal.l.o ti .
196, ! Na. ~. a Pp ~~ 2.1.0 ~'~
~~ TEXT: ~~~ Folygonization is the formation in the gra~tn off' subgrains ~ ~ _~
- ~ wi'th their own orientations � The authors discuss this ;~nenomenon ~ ''
~; w~ich~was first observed in 1932 (Ref.1} and the simi:la;r effedt
I called "recrystall,~zatioxr in s3,tu" (fiefs 2-~} The p~~p~~r is mainly i,
~ a critical literature survey. the authors maintain tha~~
Pa Ygoniaation can be correctly explained only on the b~~sis of ~ :~; ~
dislocation theory, as showr,~ schematically ire Fig.2.
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A1J1"ISOR: Oding, I. .~,. , Cr~1~.rr~~;,;ur~il.xri~; t~IFvn~~cr AS IJSSii
T:~TLE: International Symposium of the ~~atigue Strength of Ls.xge
Size &Tachine Units
,~
PFRTODICAL: Veatnik Akademii Houk SSSR, 1960,~Uo. 12, p. 91
TF,XT: The International Syc:posium of the Fatigue Strength of Large Size
Bdachine Units took place at Prague from September ~ to t 0, 1960. ~'he
lE:ctures dealt with prable~s of f~t.gue destxuctian, the action of mctai-
lurgical and technical factors, and the size and shape upon strength. A
campreheneive report w~.s delivered on each of the pxobleme~ The discusW
e~.an wgs eynohranously translated ~.nta five la~iguages, A new metallur-
gical plant at Gstxava and the Scientific Research Institute of Welding
in $ratislava were inspected.. At the close of the sympasiuw, the Anni-
versary ~?edal of the Higher Polytechnic College, Prague, was awarded,
anrnng oth,r persons, tp the Soviet research scientists Ye. P. Unkeav and
I. A. Oding.
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t
Th� Nature of the Scale Factor at Cyclic Loads
(R f
s/n~2 ~a%~~/c~c~9/c~aa/a~ s
~o~~~o~s
e}o ~~~ that .for small s~mplas a slight deformation re
in she surface layer, ~ehich leads to an additional in gistance ex7ets
fatigue limit for small samples, Ire contrast, to No NpcDevase of the
A� Wel1e (Ref, 6)e and Ye, ~, a idenkov (Red
opinion that the elastic ever Shevandin (Ref. 7~ ~4)x
gy of the sample is~nothe author zs of the
ing the type of the scale factors suitable for defin~
Lion of the tyke of scale factor bynmicrocraeksaacopinion, an explana~- ,~~~
Lavrov (kefo B) is not suitable either eo.rding to fir, ~, .~
ly reduce the strength ~ do not cecur in mostemetal~cuaeks v~hi.ch effect~.~~e..--.
structione Since many :influences affact the scale factor ~n machine can�..,
experiments must be conducted in the authorQ ~' systematic:
the scale factor p.roblem9 and laboratories ~'ouldihave to order to sol~re
where eompari$on tests can bc~ conducted on large and mo Parti.eipate
There are 8 references; 5 Soviet ~ s al.l samples
ASSQCIATION;
U9g and 1 Germane n
Institut
Metallur
Card 2f~
metallurgi Akademii nauk 3SSR (Institute of
y of the Academ of Sciences USSR~"~`"_
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s/'o~2 60/o2~~'ao~~/`QOa j0~, s
g0~ ~ Bogie
RUTHOI~ ; .~ Oding ~ I lc~
TITY,E: The Idature of the S~:al.e F~s.ctor at Cyclic Load~~s~
.'~
PEP:zODICnL: Zavadskaya laborator~.ya ~ 1 g60 ~ j~ ol, 26 ~ Ho~, 9
ppa 11 C~6 M 1107
TEXT; The influence of the sample dimensions on the metal strength is
influenced by various factors depending on the teat conditionay In the
present papery the author discusses the factors which ~iay be con8idered
to effect a reduction of the cyclic strength at an increase of diameter
and thickness of the sampleso In a pxevious paper (Rafe 3)~ fi.~re factors
were already mentioned by the author, which wexe used for spec~.fying the
scale factor, iged~ #,he metal quality, the tension gradient~~ the hetproM_
geneity of tensions s.nd mechanical properties in the micro~rolumes of the
meta~:a the technique of sample preparation and the total influence of
the cyclic tenacity and sire of the metal granulationo In the present
caae9 these factors must also be conea.dered apart from the tension gra~
client, and it must bE~ added 3,n vie+~ of the statements by Hollornon
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2~36t~ s/12~~/520ooo%e~/o~~/~~~+
A052/A101
Mod:lficatioi'� of som~g physical prapertie~s ... -
cau;acs a sharper de~~rease af. plasticity of microsampa$eem&1a e~ whenestudyingie~d
cha;^acteristics, T~;;mamieal method of measurement P Y
temperature relations and changes of E and internal friction. For iron the peak
of internal friction was detected at 110 ~,~ testa etof oreepnein thedstageof
max s decreased by :3~ by the end of the fi g
No maximum Gf d~sarement ~ was
the ste~.dy creep max $ underw�nt na changes,
cbs,ez4ved with chram~e-nickel alloy, hawevex in the first stage s decreased rather
considerab~.y ~appro:ximately by 50~). In the case of ~.ron E changed slightly,
whe:rea.s in the case of chrome-nickel alloy it changed considerably, Passing
thr,~ugh ~fhe maximum. Sn corm�etion with the deduced law~r of changes of internal
fri,~tion at creep, conclusions are made on the decrease of density of disloca-
tions, prepared far mot~.on, at the first stage o~ ct~mber ofssuahsd slocatf~ans
second ~t~age, and an a continuous increase in the n
1n 'tha praeess of aaeelerated ex~eep. In the author~a~ opinion the results of the
inv~estigat,ion confirm experimental?y the main thendensityooftdislocation$1with
theory of er�ep, as to the ].awe of ehang,es i
stages of" creep. There are 1~ references. L. C~etsov
~Abstracter~s note; Complete translation]
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~Y
a~5~/A~~1
~~ ~~'~~
R ~}ordiysnko, L� K.
Odin~,1_.~x-t-----� o series o~ metals in the Process
A~4RS ; - s ~. c al pr P
soma p~Y
Tl'I~E; ModificE, at high temperatures
of creel 191, 61, abstract SSSR,
Mekhsnika, 'no. 7, 6n Moscow, AN
atlvny3t zhurnai, rochn. sPlavam. T.
pER1~JDlC~; Refer o zharoP
(v sb. +~lssled. P electric
g microhaY'~ess,
1~~: 3-161 and modulus of
aces the madificat ~? friction temperatures
The work inVestig intern
,t, ~ ~; character3.stics, at various stress~y-395, ~~"1}32,
mechaz~ieal preeP fasts ~N _257, sand chroms-
eoniluctivit~' rocess of to commercial iron, ES-598 alloy
elat3tieit~ E in the P EI-~37B, m1ero-
tests refer the
.. affecti~
to 7 C. The ET-395, ~ 432 lace in
up ' ~ EI-257 take p
~~ -598 f no struotur~ miQ ohardnesa a,~iess decreases,
~'N -437 , xn the ease when es o
substantial chan8 first stye the micr0h es in the
nickel alloy. in the
s,re PTesent' creep: sensitive to chan8 creep strain
hardness third stE~BeS �f is mOSt with an increased
first and increases. Pla5ticre~idual stress
in th$ third it The in4rsggc of
Process of Cpeep.
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a~o~o
s/z.~o/~a/moo/o05/00~/o f 3
Certain Re:lat~ans Gavernin~; sang-Life Strength
~xper.imerital:l.y~ Therefore 5 a very simple method is proposed of
df:termirii.ng the caeffica.ent of reserve wark~,rzg ability of the
metal. ~' , which ca~~ be expressed as +,he reserve service life
four a giLrFn stress a.rld can also provide a p�7sibility of
calu~.ating the strength reservE Pram the reserve of service life
S~ructu.::~es in w~~ich ~i,he .nefial ~'la~, az~. F=c~uai. proneness to darraage
w~.ll possess p~qual s~Jrength reserve values., The distance /
between the l.i.nes of equal proneness to damage from the failure
~..nea wi 11 di_f'fer .for. various metals; depending on the intensity
a.f accur~ula~tian of damage,. The proneness to damage of the raetal
~.ri be ~~~cpre ~ssed as t,Me r~~t i. a u f the ~~r~r~ t ,sex~v ce tame a~t; rz
~;1.1~~:n ~t~~~~~a~~ t~a i.~t~s ~~E~rvlcti ~.if~r ur~t;~..~ f~~:i~lu~e a~ thc; ~~t~~r~F~ ~~k~t~~is~~
ThP here proposed me~t;had is ware ~ustifled than the current
method of r~al,culati.n~ t?~,e coeffic:i.ent of strength reserve., which
s t~~.sed ors a. constaxl+,; stress reserve far any given service life..,
There are 3 figures and 9 re.~orence>~ ~ 8 Soviet and l English,
SU~~fITT~p � ~7'u.1y ~:, ~1.g60
Gard ~-~
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~F~r�
/~.~U/~~t~~c~/C~~,~~1~i/C~~~
E~7:~/E~:S~
Cc~r"ai.n Rel~~.tions Caov~rnin~~ ~c~n~-~I,fe ~taryeng~Gh
If thc: work of a single d.i:~locat;ion is expressA~. by r_, a stz~s^4
o ~v.~17. ~~r'C-d11C:~~ tg~o. dis.~.ac~a~,ian~.5 in the avalanc.hy� 1'h~~ tot a?
zl~a~n?~~3t~ of avr~l~~rl~~kies x~r~t~u:i~z~ed far t~h~~ rr~~.;fi;za.1 to t'a:a.~. wil? ba
kr t.xp ~ ~c~)
A~: ~x~~PZ~t no data a.re ava.i~s.b.1P which would p4rmit establish~.ng
a~: ~.ura~ely the work until. f. a~.ll;r~; C du,raen~ cr~,ep 4 However ~ it
is shown iz~ the pe,per that 3 assuming; tl~~at the we>rk until. failure
i s a const~~nt value ~ the line of equal damage c~j' a given alloy
~~ equici~.st,ant to ~r:he ?ine of failure., Experimental results
repradu~;ed in the 6~~~aph.., Fi.g 7~, for, several steA~ls dnd. same oth~:r
;alloys ix~d7.cate that in all cases the lines of proneness to ~(
damage are paral?el to the lines of failure. Tr~ereby,, as the
propane ss to damage the authors aGsume that point ors the cry
cure v~hich corresponds to the beginning of the third sectian, t~
~`he sec;t;io~: of the E;urve w~.th increasing creep speed, The
thearetiwal.ly estab:Lish.ed fact that all t~:e lines of proneness
to damage: a,re paral:lel to the failure lines have been con..firr~ed
Gard 3,~
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r ~'
f~r~t"iit
s/lea/6o/aao/oa51aal/a33
Eo73/~~35
Certain Relations Governing Long-Life Strength
plasticity resource, the plastic prapertie~reg tseeedsaandahigher
better utilised ands consequently, higher p P
a:ated stresses are permissible However calculations of the
are difficult in cases in
strength reserve on the basis o:f sr
which the metal under consideration has a low plasticity resource,,
In this case the variance in experiment~rousterror5~ alnuthis paper
calculation di.fficTa.lt anc~ prone to Bang
axtother criterion is proposed for establishing thesresTh~ebgsicngth J
of machine parts operating at e~.evated tempe.~a~ure a
idea consists in selecting as the stha~g~~ ~,sl'aeconstant value and
required for fs.~.lure C, assuming t lied ~~tress~ Depend~.ng
does not depend on the magnitude of the app lication
on the magnitude of stress and the duration of sure ss app ,
if the samle work C' is
various degrees of damage may occur;
hieved for a given metal
spent, the same degree of damage will bF: ac
with various stresses and service ciux~at:l.ons,. Theny ~~he reserve
strength until failure C will equ~l (1+)
gc r ~-
Caxd 2/4
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~~~Cj
~} ~~~~u ,~073i~i35 ~ o (;too ow
i ~~~ sc ~
and gr~,dm~~n
I A w , -.~_-----
Y h , .~~'nB-~--~_~~~~~,~~. .~ fe ~txength
A elation C~ov~~'nir~g teghniche ~kikh
TITI-E= Certain H nauk SSSR~CtdeleniyP o33.-37
a Akadem~-~ 1 top1iVO~ 19~U~ X005, PP
~~RZ4D1CAs~t l~U) st~eta~-~-urg~y rs and tY~eir team
n , Ibe autho th was estab-
work of h temperature streng
In earlier of hig detert�ined as the ~/
TEXT anew criterion resource er, and an
( 1- the --plasticity stres~] cl (2) ~
Rshed~ namely, for a givers constant
~. t 1
t1~e to failure _ V1T1 ~ total
average creep speed V1 er _ Service life Is ~>,
om orient during resource is
iven c P anc3 the plasticity
Assum.~-n~ that for a ~ ermissible yvill be
Etot is P last icity re soup. ce (3 )
ds for~,ation reserve P
t;he remaining Yr
sr Y KS E~ 't
ations on the basis of the
ov.t the strength calcul
Ry carrying
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80~.~7
S/12q/6o/OOO/ojf/oo5/020
Def ~ E473/~535
.ormat~an and Failure :in t:he Case ~,f' '~'hf~rtttal FatT .
if a cotrtponez~{; is ~~rc~ci~icec; l'r. otn trtaterial w~ue
Thermal canduc tivl, t ~ th a I�,gti
is low, appearance ofafrdacturesZin thetce criterion Ba.
heating and cooZin ase of cyc~.ic
However g is tc~ be anticipated an the riljs,
a law therm7lhconductivit xs
produced from mateari.al .With
flat part oi' the component, the cracks will a
for the tested materials are Some of t PPeSx on the
he results obtained
't'here are 3 figuxes given in the papero
2 .~. table and 4 references ~ ,,
are Soviet and ~ uer~;ail,
of wh.ic;
AS;~t~~' ` ,~ t'XQN: TsNIITMASh ~
t.~
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~oz~7
~/~.zy/~a/aaa/a~/aa~/ago
Deforr~u;~tj.on and Fai~.ure in 1.he ~rxse Eo7~/E535
of xhernra~. ~'at,gue
to thmt shown in Y,,:fig 1b~ lxi the secax~d case th
tore cif the surface of the carnpoxtent will use bas tenapQr`~~.
equal and :accarditigly the temperature stresses w:illlbY
equal throughout the surface and, therefore, the above
formula does not allow any conclusion on the like:l e
loGatlon Of the Cr y
.Paper investi atedarpctangularnurisme authors of this
alloys Ex~,1~EI~~~an,~ EI~Z21~ P specimens made of the
turbines). Thsse speci>nen~ ereaheatedsin~ta for gas
a temperature of 8Q4�G throughout and were ther>l;a,t check
li~ ti
cracks at the surfaces of edges and not at the ribgao f~r //'
prisms, In the most ~.ntensively cooled the
Prism (ribs) the increased ductilit parts of the
positive infl~xence rn the res~.stance Poo'ved to have a
Apparently cracks o3x F: i~~~ cif rack format.ion.,
m$tal,r of lcaw tlxert~3a 1. cc~nductir,i.t~ts made of refract:�ry
the presence of stre.~s conrentrators1lthE?n2~Ga~rtcnf ~, d'4e ~,
hard 3~~ stresses exc :ed '-~~~: u ; ~�E_, ,.=a t.;~ u~ tkie basic: r. ~x ., rrax,+:
~~
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- nai~~i~ ~ - r~~n_arltvssa_nn~~ ~ann~ ~~7R00041 -6
X019 bo/�0�~�~~��'~�~�
5~~3% 53~
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mal ~~aL"~'` a ~-"`''
of Tl~er ~ to/~~R has
e is the Gas� t of h�at
d gai ' n,-~e critEr3. ~ he coe,ffexkan R is
a u~ d
D~~or~gi,t].DY- an the h`''at e'.{eha tiq~' ~' i heat trans t . The
that this e~1ua L,en~� of cortponen erta~-n tine ci
va~.~xe. ~~ the c�e f fit ~ioii �~ the d after ~' c tiiustrat
re1ease~ ~ i~ti~ rYj,.ine~' afore f~.el~ rgce~s ig he~3t
aster temper LiTt~ p cieTxti �~' Z~.
char the e coq ef~.i Vii.
a er of of th ~,gh ca item�~'
charact be~inn,~.n~ with a h the rr th the d wi11 proceed according
to tha 1.r>lws of c,or;
only
less drastia9 so that in mangy
re often ti~.e
Card
if ~ mo
are
detect
are formed, ~-rhich are not easy t
f the cyclic temperature variations is ~
only result o
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APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

~QY~~2.,~1..7M~9f `.i~
ABTiiORi: gsiingf '~+ ~` s
TpNtin~ r.~f '~I.~xb~.r~~ Var~ee iz~ the G ~ek~ ~r~a2ovotn pct ke~p~~remenw
T~T~~S , ~ #r~ni o t,~~rb~t~nykYG lap
tx o~ (~~,~ y : ~,,
riot' te~npc~xa tug�;y ~ _
~: 8l ~.�1.bOX'F~tt~l`~.yaf 1~~~Jf 1~0~. ~~f ~T ~f p~ ~~5w~6~ (U~Sa)
PERS~~ICAL: Zavodsk .Y
A ~ sclf~~. methrad r~.r.:i arrangement UPT for t8,3ting turb3.ne ~a'anss
ABSTRACT: p
and samples at varying tem;peratuxes a~ the ga.e c.ua~'aas turbine
worked out. `1'ha device (Fib 1,l isf in pr~.nciple, ~
whexe hot g~,s enteTS can the Gr~e ba$ampntime; hattgaso~idxs.i~'
dour samples can be tested at the
Flaw art~und them ~,1t~ernatelyC The automatcPRhlftT~.rbmn�avanss
'~ ~- 9 G~r~'ied out by A 3ervc~mQto
air cup. ren L whi ie 'thr~ tempera�
(~i~ 3) were tested cn a, n3.okeQQb~~� ga~,~6inrreased to ?aQ��
t.ure was xeducsd from: 75a tle ~ as msasuxed by thernocoup~,eso
The temperature oY Vhe aat~p
In the course off' the test the samples wer~ tensiledstresStoYi�n;
m and
the xa~;lax showed a rate of 750 rp f
Table
28 k mru2 webs obtained. The testing xesul~ackstatn554C- ~Am
~~
Card 1f2 ehaw that the samples showed no eur~'ace c
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APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

AUTki4RS: gclin~, I ~ ~ z ~ Frf-~.:,s.n, 7.. ~,
iI'rLL: `i'he Tni~~ortance o1' aur� in alo~~r 17u~t~.-res of 1~iE:tale ut
Creepircr- Conditions (itol' ~;ovr,rkhnostnykh sloye�~ Lori dlitel'nom
razrushcmii me tallov v uslov~. akh polzuchesti
PEitIOAICAL: ~avodska~ ~, r.~~~ox'atox~.,; a., 1 ~ j; q Vol. 25, ?~Ir 3: ~�T> a29--~:~2 (U~~1~}
!i~a'I'1tACT: The fact thr-t ~alaatic de:?orm~~'cions take pla~,e under c~~~her.
enorgy conc~i bons in tl-e surfxco la;;fer th~;,n in lovier : ayt~r:~ is
o~.' especial im~Joi~tance fox dur~.bi.lty te:~t::~ cif iinr:t-s~~sui..,tr~nt
m~:ts.1N. In metal -~~iork:ing iind~r cr~je~~ing ec~ndz t:ion.c~ th:r infl.u.cnce
of: the surface la;~er ~le~}ends ms,in2~~ c,n +he' sc~tiic-f~~.titc~r (I} i.n
th� case of small-dimen9.zonal oamf~las. `Phc inf'luPnce ~-f (I} an
s~~mples ~~rith -~ iliickne:s~ of { ~ mm h~,s so �ar r-ot y-yer~ examined
s~rstc:rnatzes.llSr. Tn the cr:LSe undo/ discussion flat sam~lles
(~~ig ~ } of anneaie~d, roof 1~ steel containint; carbon (i; ~ 0. 1 a e,
b�n - G 3g , ~i - C~.42'~, .:3 - 0.43 , P - 0.02`x} ;ere i-i~�estigated.
The tl^.ickness of tl-c: :~~..axflea yr s changed From 0,15 to 2.0 ~
0
atxd the .xeeiaf.nt; torts tv.~re ~~.~~~~i,d nut a.~t !50 and si.resses ow
Card 1~2 22 to 27 kgfmra~: Tile creEpi.n~~ curves (Fib; 2} ;nd ZnuirE~ (Tahls~
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67,32
Variation of the I~~~chan:ieal Propert~,~;s nd ~ X80 ~9~~~-$/31
Metals during Cree~> tructure of
ThBre a.re 12 figures s.nd ly references, of wh~.ch 1~ are
Soviet and ~ English.
~U~M I~~~D s June 5, ~~~ ~~
;~
Card ~ x.,/12
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6~~3:~.
sov~~8oM59~~~8f3:L
ye,riations of the Mechanical Properties and riicrvstruc;ture of
pietals during Creep
primary creep stage, plays th,e deczsivH par9: in the
process of creep of this metal. :~) It has been
demonstrated tb3t the structural defects fa~~med 1n the
early stages of creep can be revealed by me~~ns of roo~a
temperature tensile tests, ~c~nductpd on Iasi, pisses cut
out from the creep specimens and followed bar examination
of their microstructure. ~~) The fact that the
accumulation of the structural defect: begins alread;Y in
the primary creep stage, has been proved, ~) It ha,s
been det~�nstrated that the d~,sc-shaped micro-pores,
farmed in the metal in the planes perpendicular to tla�
direction of app? ied Jtress, constr. -fiats the potentia:L
nuclei of rupture of metal in creep; micro-pores of this
description, present in the rou~marcial grade iron ta:>ted
in creep for lUt~U hours (~i0 aC, d =- 13 k.g/~eun2} and then
subjected to a room tomperat~~r4 tensile tas1,, ar�
Card iZlustratad i,n dig 1~ (x 204C-} showing: (a~ a micro-�pare
l lAl2 a t the grain boundary; (b) s, micro-pore in the inter�ior ~
of a grain; (B) s. micro-patsy revealed after the tensile
test.
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~i~+l" ~%
~! ~J~:
~$ria tior~ o f ~ ~ ~ , 5oV/~.8i~~.5~~b,98i a;l
~k~.e M~�hanicax Propex�t:~es and ~iicrvstru~.t~.�;re of
Metals dur~.ng ~raep
phase is prectpitat,ad a ; the grain boundaries, ani the
formation. of the grai~.mbouz~~ry defects is intens~,fied
{ dig lIa) . In this stage of creep ~ nuclei r;,f inter-
cx'ystalline c;rat~ks are fox~~ze~.~ wY�~ic�h a,rs rs~ealed after
subs �cti;~g tt~e specimen to a ts.~as~.le test ~ Fig llb) .
Met~,l~.ographit; e~camiraaati nn ,~f' spec;~~nsns of the Ni~C~
8.11oyq t~~este~. in 4x�a~p under higc~~r applied stressesy
Y~.e~.ded simi~.ar rasulta. detail ~d analysiq of �h~eir
experimental dates. r;:~z'ela~ted w~.th the thaoy~etica~.
considerationsv 'led the auth,~r~ ~~; Se,~eraa~, Conclusions.
1) The r;3~t2~.ts obtained in the r~~-~,rse of the present
invest~,gat~ion have rev~ea~.erl a close-~ relationsh~.p betwe�n
the vax�:~ation. of the mAaahani,c;al pr~~perties of a metal
dur~.ng creep and the d~l~xs~.ty~ of d~.s~.ocations in this
metals and cr~n.fir~ned the :~asic p4stui.a'~4s of the
str~uetural thEOry of creep regarding the laws which
govern the vax�iat~.on. of trie density o f the "ready tc~ t~OVerP
Card dislocations d~ur~.ng variaus stages of creepo
10/12 2) It has been ~astabl~.shed that intergranular plasticity9
developed in t:ha cari~nercia:l-gr~ de i,ran duri~~g the
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~ r~
variation of the '~eor~an:i.~.al Pz�vperties a~, M~~rvst~ao1~~ar$ of
Metals during Creep
amount of tw~.n.~lin$$ a the ~.arge grains break up dur~.n
ores and aftex boa h�urs at ?50 aC u,nder ss ~ 1~+ kg~mm2
p9
the structure ~.+a~ames more un~.fQrm Fig lQa,~; is~ t~la
case of this allcyq the forr,~ati.or. of defects during alb.
stages of creep is most pronv~.nce+~ at the grain
boundaries axa~. is shown up b~ broadening of the grain
boundari�s} as indicated by arro~s in Fig li~ao ~ha
presence of these grain-bounda~t' dsfeots is olearly
d~onstratsd by the appearan.c~e ~-f the mio~o atxuoture
after the tensile tewt (.gig x.01.} w~`~.oh show,s~ alsog that
this affect is most pronoYant~ed t~~ the layers which ix:
the as�quanched ,spey:unenp consisted Gf the ,small grains q
the b~aundar~,9s aetwaan grains fQrme3 a,s the result of.
break~.ng up c~' the large grains being apparently more
~�es~,stant tca de~vrmat3 on, thus ~ eaten after creep test9
fv~,lowed by e, tens~.le ~~est�~ trie aii.vy still presex~~as its
"fibroust' st~:~ctur. e7 the a:~,tex~~t~.~e layers be~.ng
9/12 Ohara at�r~,xed by the pres~~ce or ~,bserce of the g:~ain�
bo~.ndary defects , In the sperimex}. subs acted to creep at
75~ �C fox 1a0o hours (~ ~ l~ kg/~~}~ the ;yecvndaxy
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/~~r~~~j~~ Q/
~VY/~V~"`~i~'"'r~'"'V~/ ~l
Variation of the Mechanical Properties and Microstrut:tura of
Metals during Creep
situated at;~ ar near the gamin boundar~,es) had appeared
in the material. When' the miorostrutatura c>f a spaai~en
(tasted at NCO nC under l3 kg/mm~) which h~td entered th�
secondary creep stage (1Q40 hrs~ was examined, these
defects were visible even before sub eet~.n the s admen
to the room temperature tensile test~(Fig ~~a); however,
the tensile test revealed a ;large, number off:' 'anew" ;aiicro-
pores ~rhich in this case were present also in the
interior of the grains (Fig ~6b) . The results of the
metallagraphic examination of the Ni-Cr spE~cimens pare
reproduced in Figs 9-Y1. Th:is allays in tb~e air-q~~enched
condition, constitutes a partially decomposed Y �olid
solution~~, with same of the precipitated paz~ticles of
titaniclm , carbo-nitr'idas clearly visible in the int~arior
of the grains (Figs qa and b). In the maizi,~ hawav~~r,
the a'-,phase is f,n the state of fine dispeaPSlan anti is
not re~~olved even at th�, magn~.ficatipn of ~?OOa; the
Card characteristic features ' of tl~e alloy in th~~ as-quenched
8/12 condition are the presence a,f alternate la;~'ers of :mall
and large grains (fibrous st,ruature), and a~ certaiYi ~~
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

67'g32
OOV/180-a9-b-8/31
gariation of the Mechanical Properties and Microstrucivure of
Meta~.s during Creep
~ic~�ostruel;~ire of the invest~.gated r~aterial:~ before
creep tests, f`~mediately aftEtr the creep tents, and
after the t�nsile tests, was studied. F~.g ~i shows the
structure of iron in the norn~ali~ed ~onditic~n (a) and
after a room temperature tensile test fib); in the
latter case, th� grains b�eame elanggaced in the direction
of the applied stress. (It should be noted here that all
mierophotograp:h,s in the present paper are reproduced in
such a way that the long side is paral~,Q1 tc- the
direction of the appl~.ed stress). Fig 7 shows the micro-
structure of a;a iron specimen (a) tested in creep (~OOoC,
a = 13 ~g/mm2) for 204 hours, and (b) subse~~uently.
sub~eeted to a tensile test at room temp�rat;ure. .It will
be seen that when the creep test had been irtterrUp'~ed
Card during the primary stage, no structural changes could be
712 observed in~ thr~ specimens (Fig 7a~ ~ however, when t~1e
structure of this specimen was examined after sub~~~cting
it to a tensile test at room temperature (Ff.g 7b} :JLt
became evident that already i;n the pr3.mary creep s1;ag�,
permanent structural defects (in the form of micro-por�s `~
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

,'~�
b7832
sov/18o-59�b~~3/3~.
Variation of the Meeh~tn~.cal Properties and Micrnstru~ture of
Metals during Creep _ ,
early stags of cree (primary stage and ,the beginning of
the secondary stage; as in irony elongation decreased
and tJ.T.S. increased, ,but in contrast to 'iron, the
proportional, limit increased, the creep curves of th�
~~.-Cr' alloy' ~ tested � t ~,~0 aC under the appl;lied stress
of 14, 1$, and 2Q kg~mm ,are reproduced in digg 5b. In
Fig Say the prapexties (o~ ~ c'~ , ~) of 'the (~iwCr alloy
tested in creep apt 754 �~ for ~OQ hr, are plotted against
the stress, v~~'~applfi.ed in the creep test. f (the values
of these pr~pper~ies at .~Q~ = 4 correspond 'to the
on"ginal properties`;Q~' the. a11oy),. , It will be seen that
al'thou~h~ the propert~.~s of the metal before and' after the
creep tests; were. dif~,�rent , th~a magnitude~.o.f ,this
difference was haxdly ~a~'f�cted by the m~gn~,'~ude of the
stress appl i~d in - the ~~ Creep tests . Thi~~.~ is attributed to
the fact that in �sth~s~~, case, the duration of the primary
creep stage~,(whichtdetermines,~th~', magnitu~,Q, of the change
Card in .the mech;~nio~l rp`~o~,perties ~ of the a11oy)� spas .
6/12 practically unaffected by the vari~tion~of the applied ~~/
stress , In the next series of experiments: , the N
~a.
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

6~$3z
Var:tatiou of the Mechanical Propex�ties and Micr s -8/'31
Metals dus~.ng Creep true.ture of
It will be seen that with increasing magnitude of the
applied stressp the duration of the primary creep stage
increased from ~0 to 350 hrs, the total deformation (~}
increasing from 0.0~+ to 1.08'. Fig 3b shows how the
carious mechanical roperties of the material (me~~sured
after 1000 hr creep varied with the variation of th�
applied stre.sa ct~ (the values at v~ ~ 0 eorre-spond
to the properties of iron before the creep test). Tt
wi11 b� seen that U.T,~, of the material was not
off�cted by ;inc:reasing the applied stress from 8 i~o 13
~~'/~~; hawlsver, with f.ncreasing ~~ (and there!'ore
with inereasang~de~ree f total deformation;9, ~
d�er�as~ed an~~ p~ and ~ increased. The c:re�p 'curve of
the Ni-Cr alloy tested at 7 'd oC under . Q ~- ~.4 kg/mm2,
Card shown in Fig .~+ bottom curve, is character9lzed b a
Z/12 very snort primary s,t~t'ge and by a relativel3- short
(340 hr) secondary stage: The ~~'fect of t~~e duration
of creep on�elongation (8), U.T.S.
li~tit (c~n~) ~.s also illustrated in F~~')~.an~,np~hportional
too, the mecr~anica].~~ p3�op~erties changed mainly initheaSe
_ .�
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6as~z
Variation of the Mechanics' . Froperties Oa~dBMic gost~~/31
Metals during Creep ~cture of
of creep. 83.mi~ ,. ~,~ although more pronounced, results
'~eY'e ootained whE~ta a slightly higher strea~s of 1,3 kg/~2
?~='~I,s used in the creep tests, In this cases the increase
4n the yield points after the primary creep etag~e
umounte~. to apprc~xima tel ~
prom 2 ~ t~ 4 0 ~ ~ ~~/mm ,while 8~ i~~creased
~; since in this cases the total
pl~aatic de~'ormation at the end of the pr3~~ry stt-ge was
th~Yee tomes larger than that in the Case o:~ the ,~pec~.men
tested ~;.nder 12 kg/~~, the object of the a~ext sE~ries of
experiments was to compare the mechanical ~~ropert;ies of
specimens tested in-creep under various applied ~~tresses
and consequently, Characterized by different degree of
total deformation at the end of the primar~~ tree ~ stage.
To this end, four iron specimens were test~fd at ~04 oC
and�r $, 10, 1C, ~ and 13 k mm2
test be~.ng 1000 hrs. . the abt~in�!d duraticln of each
reproduced in Fi creep curves arc
g 3a, where elnnget~,o;c (s, y~) is ,plott�d
Card against time ('~, hour's); the broken line connects the
4/12 points at which the primary creep stage ended; the
appl~.ed stress: c~, is indicated by each creep c~:rv�, '
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

- nr-ate-;ice -~ - r =~c~_
67832
Variation of the Mechanical Properties hand Mf~p 6�8~�~1
Metals during Creep astx`ucture of
eac~i cr�ep test and after the tensile tests was examined
longitudinal microsect;iotts having been used fey this '
purp�s�. The results ox' the first series laf experiments
are reproduced in Fig 2~ where all the me~l~ani~a,7.
p~`aperties~ listed above, are plotted agai�st thls
durati�n t'~, hours} of creep of Iran at ~0!) aG u~
applied stress of 12 kg/mm2~ Eder the
is the creep curve of this materialoob~a~.nr~d uft`1C} curve
conditions. Zt wiYl b~3 seen that most marked eh~-r eseaf
the mechanical properties were observed in file m~~teria
which had dust entered the secondary creep sta a the 1
duration of the primary' stage being approx~.ffia,tel -`2 0
at this point, a sharp decrease in the plas~ticity~ of irony
as characterized by ~, occurred, as well as an i~;crease ~
in the yield points and in the ~ralue~ of bs. In the
initial stages of the secondary creep stage' b sli ht
3/12 increased and cgs Qg~ and 8G slightly decrease g ly
after which all these properties r~aained ~ d,
oonstants practically rio change in the U~Ti3,~was~y
observed either in the ~,
primary nr in the se+~oxu~a,r,~ stages
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

~~~~~
Variation of the Mechanical, FPOperti+es ACV/1~0"596-x3/31
Mdtals dur~,ng Creep nd Micrastxu~~~r~e of
iron, and at 75a oC :fin the cary~; �~. ;; ~~..,~ ,Y
The effect of creep on the ~:echdr~ic.~;i ~~ ro Ear s.a.loy,
these alloys was studied by so-calked ~mic~`o~fe-s of rr
mdthad which consisted in condueta.ng mechax~iem�chanical
tensile) tests 8n small specimens cut ou al
creep test Pisces its .the manner show~a in Fj,g la � nth
s,t~apg and dimension
sl~own in Fig 1~. Ibf or~erf the micro-spec.imen~~ arse
s~tres~es due to the maachinin,gcore~te the xesidt~al
slpecimens were annealed for 10 hoursiat9~UQeoCirc>n micro-
c~~s� of th� Ni-Cr allay this treatment was .f ounal to bhe
utaneGeesary, The rate of strain of 0 e
employed in all tensile tests. 'S ~'~min was
dj�ggram? the followin From the stress-strain
g properties were d~,te~rmin�da
ch, - u�T'~' ~kg/~~~~ as and ~~
points, respec~Cive1 ~ 2 u 'lower ar~c~ upper yield
Card the plastic region ofCthe~ }} bg - relati~~e leligth of
2/12 b ~- elongation ~~) . a tress strain die@;ram. ~~) �
At the same time the mierostruetureooflth~l~t t~$/mm~).
e al,1Q~s aft�r
APPROVED FOR RELEASE. 06/23/11 CIA-RDP86-0051 3 8001 237800041-6

i~ 9,~, v~
.~: ~_ T~ Y. end ti~~ ,> (M~'sf~c~~r~
Variat~.cn of` thr~ Mechan.~.c~xT. ~r ~~~~~s ar~c~ ;~',:~.cr~ra~;turc `,'
~of Mewls during Cr~ ~~~.~ _-- ~..
PERZ~DTCALs ~xvestiy'a ~ademii z~-uk SSS~~gtdelen~.ye tek:hn~.eheski
nau~,Matal~.ur~~,ya ~. t~ Zi~.r, ~ kh
p r `3~