SCIENTIFIC ABSTRACT KURDYUMOV, G. V. - KURDYUMOV, G. V.

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• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

24-6-2/24
Regularities in the kinetics of martensitic transformations.
(Cont.)
the process of formatioa of the nuclei. Thus, thermal
motion appears to be one of the main factors which govern
the kinetics of martensitic transformation, as well as other
phase transformations.
The alloy of iron and 2& Ni, ~4~ Mn (5). Isothermal
transformation was investigated in'the*range room temperature
to -130 C.. As the temperature decreeLoes, the initial
reduced speed of isothermal transformation, given by
N I = -L ' dV%l 100
Vol ~ dt/ t = 0
at first increases, at -50 C it reaches a maximum, and
thereafter decreases and has very small values below -160 C
(Fig.1; where V - volume of martensite, formed at the
starting moment of the isothermal process (in %), V' - that
part of the volume of the specimen which can be traRsformed
at the given temperature (in %-), t - duration of the iso-
thermal proceBS). If the low energy of thermal oscillations
Card 2/5 is the factor limiting the speed of formation of nuclei on
the low temperature side of the maximum, then the rapidly

24-6-2/24
Regularities in the kinetics of martensitic traasformationB.
(Cont.)
increasing work of formation of the nuclei,with increasing
temperature, is the corresponding factor on the high
temperature side as shown in earlier work of the authors(6,7).
Steel 85F 22' containing 0.85% C and 2.2% Mn, Bee
Pig.2 (G'?, 13). If the cause which makes possible
observation of isothermal transformation in the temperature
range approaching -the martensite point is the high work of
formation of martensite nuclei, an increase of the trans-
formation speed should occur with decreasing temperature. To
elucidate the Iroblem the experiments were made with this
steel, the martensite point of which is about 155 C. It was
found that in this steel the initial reduced speed of iso-
thermal transformation N' increases at first with
decreasing holding temperatures below the martensite point
and then becomes unusually high in the range between room
temperature and -50 C, dropping sharply with further decreases
in temperature (Fig.2). It is concluded that the absence of
isothermal transformation at room temperatures, and the
occurrence of the transformation on cooling only, is
Card 3/ 5conditioned not by some non-thermal process, but by the
higher speed of thermal formation of martensite crystals.
M

24-6-2/24
Regularities in the kinetics of martensitic transformations.
(Cont.)
Steel containing 0.9526 C and 3.5W Min. (Fig.2 ref.14).
Isothermal formation of martensite in this steel was,observed
in the whole temperature interval of wartensite transformation.
This case is denoted by 95 r-3 in Fig.2. Maximum of H1
occurs at +250. 5
Fe-Ni-Mn alloys (shown in the table on p.? where the first
column gives the Russian designation of the alloy and the
last column gives the wartensite point). Fig-3 shows the
initial parts of curves of isothermal martensitic transforma-
tion of the alloy H24 rs (23.8% Ni, 3.2% Mn) - where U
is the amount of martensite, t - is the time in minutes.
Fig.4 shows the temperature dependence of the initial speed
of isothermal martensitic transformation N, for Fe-Ni-Mn
alloys having different martensite point T t is the time
in seconds. The changes in TM have no effect on the
position of the lower bemperature limit3 of the transforma-
tions (for the three alloys), they all lie near the boiling
point of nitrogen.
On the basis of their own results and literary data, the
Card 4/5 authors conclude that it can be considered as a well proved
established fact that the temperature dependence of the

24-6-2/24
Re laritips-An the.kinetics of martensitic transformations.
(ront.) - -
speed of transformation of austenite into martensite is a
characteristic feature of all phase transformations. Thermal
oscillations of atoms in the lattice are therefore one of the
basic factors determininG the kinetics of martensite
transformations. "Athermal" transformations are in reality
the result of thermal formation of nuclei which takesplace
at very high speed under certain conditions (low work of
formation of the nuclei at large degrees of super-cooling,
hi8h energy of the thermal oscillations at temperatures which
are not low enough). Presence of locations which are
11prepared" for forming nuclei lead only to an increase in the
temperature at which nuclei would form at these locations
owinE; to thermal fluctuations.
There are 5 fi6ures and 38 references, 24 of which are Slavic.
SUBMITTED: March 20, 1957.
AVAILABLE:
card 5/5

AUTHORS: Kurdyumov, G. V., Member of the Academy, 20- 114-4-25/63
Makilm-0-vii-j-07-T.-i Nikonorova, A. I.
TITLE: The Activating Influence of Plastic Deformation on Martensite
Transformation (Ob aktiviziruyushchem vliyanii plasticheskoy
deformataii na marteneitnoye prevrashcheniye)
PERIODICAL: Doklady Akademii Nauk SSSR, 1957, Vol. 114, Nr 4,
PP- 768-771 (USSR)
ABSTRACT: The present paper is intended, among other things to confirm
the opinicna on the influence exercised by stresses on the
activation of the transformation. The authoTs investigated
the rules of the restoration of the original stability of
austenite on the occasion of annealing at gradually iucreasing
temperature. The change of the stability of the austenite
resulting from a plastic deformation or from the following
annealing was judged by the strength of the magnetometric
effects in the temperature domain below room temperature on
the occasion of the transformation of austenite intomartensite.
It was assumed that the activating influence exercised by the
deformation can easily be determined in such alloys which
Card 1/3 possess sufficiently marked elastic properties. The authors

The Activating Influence of Plastic Deformation on Martensite 20 M-4-25/63
Transformation
therefore selected iron-chromium-nickel alloys for the
investigations. The composition of the alloys used is given.
In the case of both alloys the resistance of the austenite
changes inhomogeneously with an increasing degree of
deformation. The following was observed at increasing pressure:
At first an increase of the intensity of martensite trans-
formation compared to the non-deformed state took place, then
the activating influence exercised by deformation became
weaker and above a certain pressure the martensite trans-
formation was slowed down. Such a character of the modificat.-L7*
of the resistance was observed at 200, 1000, and 175'C. A
deformation of 5% increasesthe martensite point as well as the
amount of martensite considerably. After a deformation by
7,0 the total amount of martensite increases to 20, and
with a further deformation the transformation effects b~,come
weaker. After a deformation of 14,7% the effects are already
weaker than In the initial state. When annealing at
temperatures of UP to 4000 the resistance of the deformed
austenite increasesbut when annealing beyond 4000 the
resistance decreases. The activation influence exercised by
Card 2/3 the deformation seems to be subjected to the occurrence of

-.,K=YUMOYJ----0,eV-, otvtjtstvenrqy red.; SAHARIN. A.M., red.; SHVARTSKAN, L.A.,
red.; MALKIN, V.I.. red.; GOLIKOV. V.H.. rad.; WEZOVA, V.A..
rod.; CHBRNOV. A.H., red.izd-va; SIMKINA, Ye.H., tekhn.red.;
KASHINA, P.S., tekhn.red.
CMetallurgy and physical metallurgy proceedings of the Conference
on the Use of Radioactive and Stable Isotopes and Radiation In the
National Economy and in Science] Hatallurgila I motallovedenia;
trudy vaesoiur-not rauchno-tokhnicheskoi konforentaii po primenenitu
radioaktivnykh I otabillnykh izotopov I izluchenii v narodnom
khozisistva I nauke. Moskva, Izd-vo Akad. nauk SSSR, 1958- 518 p-
(MIRA 11:6)
1. Vaesoyuznaya nauchno-teXhnicheBkaya konforontaiya po primenentyu
radiaaktivnykh I stabil'Tqkh izotopov I izluchenii v narodnom
khoz.vaystva I muke. 1957.
(Metallurgy) (Physical metallurpX)

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KURDY'MOV, G.V.; BILIDZYUKEVICH, I.A.; KIIANDWS. A.G.: CHERK", Y.G.
. 6anges of the fine crystalline structure dnring the aging of
nickel and iron-nickol-base alloys. 1991. po zharopr. splav. 3:183-188
1 58. (MIRA 11:11)
(Nickel alloys-Metallography)

f-, 1~j j-z' I ~ y I I ~'l (I V
PHASE I BOOK EXPLOITATION 983
Taentrallnyy nauchno-issledavateltakiy institut chcrnoy metallurgii. Institut
. metallovedeniya i fiziki metallov
Froblemy metallovedeniya i fiziki metallov (Problems of Phy8ical Metallurgy).
Moscow,, Metallurgizdat,, 1958. 603 P- (Series: Its: Sbornik trudovp V. 5)
Eds.: Lyubov-, B.Ya. and Maksimova,, O.P.; Ed. of Publishing House: Berlin, Ye.N.;
Tech. Ed.: Karasev, A.I.
PURPOSE: This book is intended for scientists and engineers working in the field of
physical metallurgy.
COVERAGE: The articles in the book pres(!nt the results of investigations conducted
by the iswaing body the Institut met;,.Uovedeaiya i fiziki metallov (Institute of
Fhysical Metallurgyi, a part of the Teentrallnyy nauchno-iseledovatellskiy institut
chernoy metallurgii (Central Scientific Research Institute of Ferrous Metallurgy),
located in Dnepropetrovsk. The investigations were concerned rith phase transfor-
mations in alloys, strengthening and softening processes, difftision processes
(studied with the aid of radioactive isotopes), and certain other questions. The
studies cond4cted at the institute by V.I. Danilov in the fields of atomic and
molecular structure of liquids and of crystallization processeE are stated to have
received wide recognition.
Card 1/8

'Problems of Physical Metallurgy 983
TABIX OF CCNTENTS:
Wenty-five Years of Research at the Institute of Physical Metallurgy 7
PART I. PK4ZE TRAIISPOMTIONSO HEAT TREAW=3 AND ALLOYIM
_Kurdyumov,, G.V., Academician, and K,3ks4-mova,, O.P., Candidate of Technical Sciences.
Kinetic Laws Operating in the Martensite Transformation 13
M-,Lksimova, O.P.,, Candidate of Technical Sciences; Ponyatovskiy, Ye.G.; Rysina,
N.S.; and Orlov, L.G. Change in the Kinetics of the Martensite Transformation
Depending an the Position of the Martensite Point and the Gompot3ition of the
Al I oy 25
Kurd,yumov, G.V.j Academician; Maksimova, O.P., Canclidate of Technical Sciences;
Vikonorov~, A.!., Candidate of Technical Sciences; Pavlenko, Z.D.; and Yampollskiyi
A.M. Effect of Ireliminary Plastic Deformation on the Martensite Transformation in
Fe-Cr-Ni Alloy 41
Maksimova., O.P. Candidate of Technical Sciences, and Nikonorova, A.I., Candidate of
Technical Sciences. The Incubation Period in the Martensite Transformation 56
Card 2/8

of Physical Metallurgy 983
'i6lovehAner, Ya.M. The Frocese of Nucleus Formation in the Martensite Trans-
f :,rr.-iation
Lyubov, B.Ya. Doctor of Physical and Mathematical Sciences, and Roytburd, A.L.
The Rate of Development of New-phase Centers iL One-component Systems
Zakharov, A.I., and Maksimova, O.P., Candidate of Technical Sciences. Applica-
lion of Neutron Bombardment in the Investigation of Martensite Transformations
Gniovehiner, Ya.M.; Landa, R.A., and Khalin, L.M. A Study of the Mosaic Struc-
f-ure of the Gamma Phase of Iron-Nickel Alloys in Forward and Reverse Martensite
Tronsforma-tJons
Mak.qimova, O.P., Candidate of Technical Sciences; Gollovehiner, Ya-M.; Lyubov,
R.Ya.,, Doctor of Physical and Mathoutical Sciences; and Nikonorova, A.I., Candi-
date of Technical Sciences. Basic Trends of Investigations of the Theoretical
Aspects of Martensite Transformations
Kogan, L.I.; and Entin, R.I., Doctor of Technical Sciences. Transformation of
Aiisterlite in the Medium Temperature Range
66
91
124
136
147
161
Card 3j6

Prol)le= of P)lysical Metallurgy 935
Bagaryatskiy, Yu.A., Doctor of Physical and Mathematical Sciences; Tagunavu., T.V...
-Candidate of Technical Sciences; and Nosova, G.I. Metastable Phases in Alloys
of Titanium with Transition Elements 210
I'Agaryats'kiy, Yu.A,, Doctor of Physical and Mathematical Sciences, Petrova, Z.M.;
~,_ind Utevskiy, L.M., Candtdate of Technical Sciences. Constitution Diagram of the
System rji-Cr-NiAl 235
f.)Uigaryatskiy.. Yu.A., Doctor of Physical and Mathematical Sciences; and Tyapkinj
Yli.D. X-Ray In-veBtigation of the AgW of Nickel-base Alloys 241
Utevskly, L.M., Candidate of Technical Sciences. Basic Structural Characteristics
of "Nimonik" Alloy
266
Rozenberg, V.M., Candidate of Technical Sciences. Changes in Heat Capacity of a
Nic'kel-Chrome Alloy Containing Titanium and Aluminum Under Conditions of Contin-
unu6 Heating 272
O.rlov, L.G.; and Utevskiy, L.M., Candidate of Technical Sciences. Electron Nicro-
Investigation of Fracture Surfaces in Steel in Connection with the Phenomena
of Temper Brittleness 27
Cn rA 4/ 8

P~oblEms of Physical Metallurgy 98,3
L.G.; Sakvarelid.ze, L.G.; and Utevskly., L.M., Candidate of Technical Sciences.
'Av. Investigation of the Surface lAyers of Ferrite Grains in Steel 287
Liu'-)ov,. B.Ya., Doctor of Physical and Mathematical Sciences. Theory of Develop-
irL,7.,ut of New-phasn Grovth Centers in Phase Transformations in a one-component
SYZA-em 294
Lyubov, B.Ya., Doattor of Physical and Mathematical Sciences; and Temkin, D.Ye.
Oalr~,_llatioa of the Temperature Range and Rate of Shift of the Front of a Phase
1ransformation in Spherical Bodieq 31-1
PJ.eksandrov, L.N., Candidate of Physical and Mathematical. Sciences; and Lyubov.,
B.Ya., Doctor of Physical and MathemAtical Sciences. Theoretical Analy9is of the
Effe,t of Alloying on the Kinetics of the Isothermal Decomposition of Austenite 317
Gruzin, P.L., Doctor of Physical and Mathematical Sciences; Babikova, Ye.F.;
bor-lsov, Ye.V.; Zemskly, S.V.; Peregudov, N.P.; Polikarpov, YU.A.; Tirkina, A.N.;
Fedorov, G.B., CAndidate of Technical Sciences; Shumilov, M.A., Candidate of Tech-
n1c&l Sciences. ArL.Juvestigation of the Mobility of Carbon Atoms in Steel and Al-
1,~ys writh the Use of the Isotope C14 327
Card 5/8

Problems of Physir.:al Metallurgy 983
Gruzin, P.L., Doctor of Physical and Mathematical Sciences; Zemskiy,, S.V.; and
T~n,~tyunnik, A.D., Candidate of Technicel Sciences (Deceased). Diffusion in Ti-
tanium and Titanium-base Alloys 366
Boricov, V.T., Candidate of Physical and Mathematical Sciences; Golikovy V.M..'
Candidate of Technical Sciences; and Shcherbed-inakiy, G.V. The Investigation of
Boundary and Volwn-A Diffusion by Means of Betla-ray Absorption 383
Lyashchenkoy B.G.; Litv-in, D.F.; Puzeyp I.M., Candidate of Physical and Mathe-
maticaml Sciences; and Abov,Yu.G., Candidate of Physical and Mathematical Sciences.
Neutron Diffractf-on Study of Permalloy-type Iron-Nickel Alloys 397
Pole6ya, A.F.1 Finkel'shteyn, B.N., Doctor of Physical and Mathematical Sciences.
The Kffec;t of Short-range Order on the Electrical Resistance of Alloys Entering an
Or&red State 419
PART II. STRENGTIMING AIM SOFTENING 433
Golubkov, v.m.; n1ina, V.A.; KritskeVa, V.K., Candidate of Physical and Mathe-
ntAt.1c,&1 Sciences; 10irdywaov, G V Academician; and Perkas, M.D., Candidate of
lion of the Physical Factors Determining the
Strengthening of Alloy Iron 433
Card 6/8

Froblems of Physical Metallurgy 983
1111na, V.A.; Kritskaym, V.K.j Candidate of Physical and Mathematical Sciences;
Academician; Osiplyan.. Yu.A.; and Stelletskaya,, T.I. A Study
or the Relationship Between Bonding Forces and the State of the Crystals in
Metals and Solid Solutions 462
Kornev., Yu.V., Candidate of Physical and Mathematical Sciences. Scme Data on the
Importance of Thermodynamic NAgaitudes in Determining Interaction Between Atoms in
Solid Solutions 485
Kornev, Yu.V., Candidate of Physical and Mathematical Sciences; and Vintaykin,
1c.Z. Determination of the Heat of Sublimation of Silver by Two Methods 494
KaminBkiy, E.Z., Candidate of Physical and Mathematical Sciences; Rozenberg) V.M...
Cand.idate of Technical Sciences; and Travins, N.T.,, Candidate of Physical and Mathe-
matical Sciences. Effect of Alloying Elements on the Recrystallization Kinetics
of Nickel, Nickeld-Ch:rome Alloys, and Nickel-Chrome-Cobalt Alloys 503
Nosova, G.I.i and Rozenberg, V.M., Candidate of Technical Sciences. An Investi-
gation of the Effect of Structural Changes, Associated with Recrystallization, on
Creep 514
Card 7/8

Problew of Physical Metallurgy 983
Gorelik., S.S.y Candidate of Technical Sciences; Rozenberg., V.M.., Candidate of
Technical Sciences; and Rokhl#, L.L. Effect of Certain Soluble and Insoluble
Impurities on the Recrystallization of Nickel 522
Maksimova, O.P.. Candidate of Technical S~-iences.. and Zakharorv, A.I. The Mech-
snism of Repair of Radiation Annealing Damage 528
Fastov, U.S., Candidate of Physical and Mathematical Sciences. Thermodynamics
of Irreversible Pr-)cesses in the Elastic Deformation of Bodies 550
Fastov, N.S., Candidate of Physical and Mathematical Sciences. Thermodynamic
Relationships for Irreversible Processes 577
Fast;ov,, N.S., Candidate of Physical and Mathematical Sciences. Some Data on the
Theoi-j of the Behavior of Macroscopic Pores in a Solid Body 595
Fastov, N.S-f Candidate of Physical and Mathematical Sciences. Effect of Surfare
Energy an the Field cfElastic Stresses in the Region of Macrostructuxal Defects
in Solid Bodies 600
AVA-IIAEU.: Libraa-y of Congress
GO/sfm
Card 8/8 1-23-59

XM=MIY,.G,Y._[KurdIumov, H.V.)-, BILIMEMEVICII, I.A. [BILIDZIUKMCH, I.A.);
KHODROS, L.G. (Khandros, L.H.); CHXfUjYY, Y.G. [Cbornyi. V.H.]
Change in -the fine crystalline structure of some heat-realetant allays
during aging (with summry in English). Ukr.fiz.zhur. 3 no.4t495-505
JI-Ag '58. (14IRA 11:12-)
1. InBtitut matalloftsiki Ali USSR.
(Heat-resistant alloys--Metallography)

126-5-3-12/31
AUTLORS: Golubkov, V.M., Illlna, V.A,, Kritskaya, V.-K.,
Kurdyumovl G. -,V'. and Perkao
, M.D.
TITLE: S_~~dy af,th,-)'Phy-eical Factors !.,.,hicl,. Betcr-,nine the
Ir
1--rdenini_ of Alloyed Iron (Izucheniye fizicheclkildi
1
fal-torov, oT)redelyayus1,.c11,,i):h. u-prochneniye leGirovannoE;o
zheleza)
1,
PERIODICAL: Fizil:a TJetallov i i.1etallovedeniye, 195', Vol 5, Nr 3,
Pli 465-433 (USSR)
ABSTRIM: This paper is devoted to -the study of the physical
factors ahich deter,--iine the hardenir,- of g.-iron alloyed
U
~.ith various elcments; considerin,--- only haardeninE; which
i_- due full- to chan6es in the fine structure of the
cx-solid solution ~"ithout any chan-ec in ito chemical
co~!iposition. In Lhe e-.1-periments iron was used alloyed
vca,ious elements; the chemical compositions of the
recpectivc binary alloys of iron are entered in Table 1,
p.4C,5. The naterial vias produced in a frequency
furnace in6ot weiL.,,hts of 25 Jkl; the in~;ots were,
cubjected to 6iffusion xinealin,- at 1200 C for twenty
hours. After lo.-.ior-enization annealin- 1.1he in
-ots were
forLed to a square 50 x 50 raa- After for6in6 most of
the in,7ot,,, viere annealed for the purpose of obtaining a
Card 1/9 unifor,',i; 6rain size. After for6in[;,- and annealing, the

126-5-3-12/31
Study of thc Factors ,-;h-ich Deter;iiine the HardeninG of
Alloyed Iron
bla,'-s wore cold rolled. "ith a total reduction of 80%
andnirom the produced strips flat specimens were cut which
wer-:~ us
::,d for Moa2,uria,~; the 1,ardnnec~- and z-lso for micro-
inve-tiL:ations. I
The alloyo Fe + 3% an
Fe + 4% Wi7 Fe + 8% Or were also hardened by quenching in
a IC~'* 1,,a(DII solution after the sD,~cimens ha,re been heated
in a salt bath to 1000 C. The alloys Fe + 390' Mn,
Fe -v 0.5% Ti, Fe + 0.60/-; 1,11 and non-alloyed iron ware also
used for studying the influence of stue-p-aise deformation
on the changes in the characteris-6ics of the fine struct-ure.
Specimens v.-ith initial dimensions of 70 x 15 x 8 .a-n
-ert~ leforaed in L"ho COLA staLe (on laborL
atory rollinG
stand) v.-ith reductions of 5, 10, 15, 20, 30, 50, 80 a-Ld
00%. The characteristic of the fine structure vias also
studied on filings obtained from the alloys Fe + 1.84% Col
Fe + 1.8% 111o. Fe + 2.280,16 V, Fe + 31% Mn, Fe + 4% 11i1
Fe + 8% Cr. bistortions of the third type and the
characteristic temperature were deteri-.iined predomin~,U-Itly
on specimens produced from pov.-ders. The fundamental
Card 2/9 methods of studyinE, Lhe influence of alloyia.; elements on

126-5-3-12/31
Study of the Physical Factors which Detervaine the Hardening of
Alloyed Iron
the hardeninG of the ferrite viere: X-ray structural
analysis and mechanical tests. The authors investi-ated
the relation between the fine crystalline structure of
(x-iron base solid solutions in the work hardened state
and alco some of the mechanical properties of these alloys.
Hardening of the alloys was achieved by cold plastic
deformation as a result of the martensitic y to (x
transformation mechanism. Fur changinG t1le properties of
the crystals of oc-iron in the micro and sub-mirro ranSes
(properties of the crystal lattice of the cc-solid solution),
the iron was ,.-tlloyed by various eleiaonts, naziely: Si, Til
V, Cr, lolln, Co, Ni, 11bi ',109 W. 33y we,=_- of X-ray structural
methods the folloaing properties of cc-phase crystals viere
studied in the sub-nicro region.,--: static lattice distortions
caused by the presence of foreigui atoms in the lattice;
dynamic displacemunts of the atoms during thermal
oscillations and the characteristic temperature; ma6nitude
of the elastic deforidaLion of the lattice caused by cold
plastic deformation. A., characteris tics of Lhe fine
Card 3/9 cr,,,stalline structure of the alloys in the hardoned state
the following were ap-plied: sizt~ of the regions of the

12G-5-3-1 /31
Stud-, of tile Phycical Factors which Determine the Hardening of
Alloyed Iron
coherent scattering of X-rays (mosaic block), distortions
Of the second type and of the third ty--L)e. The mechanical
Pro-pertiac of the rnicro-volumes viere churacterised by the
t1he yi,~ld point :_ind the otrenGth v,_C'Luc::~.. The
r,~su,l!-- led to the followin-
, ~L _, concl-,-sions:
1. A char-acteristic feature o-f alloys in the 1-ardened
state ol-btained by a hi,;~h reduction in the cold state or
Els a reault of tho y to a martonsitic transfor~.-Lation is
the low value of the re~-ions of coheren-t scatterinr,- of
0 L'i
X-rxys. The size of tlliese rc-~-ions "or all these alloys
is 'lie limits of 200 t LI-00
0 Tho obse2ved
diffe-ence in tile si~.e of tho bloc!.-.,; is 11C,'Ur to tile limit
of z~o_,~,or in iaeasurin-, tlie!a. 11cv,rever, the stren,-th
chLr_-cterictics chan;~-e wl thin wide limitc on chz~_n-in6
over from one alloy to another (ha_-dness 2 IfV between
1?2 and 3L~0; , i Thus, the
S betueen !;4 and 113 k,~/ru
grL~~at difference in the resistance to defor:.iation of
various -alloys in the hardened stat-c be att:-ibuted
to chanGerl in the sizos of the blocl:~,:,.
Card 4/9 2. The presence of various ClOrMITItS, jil th,~,, :-.olution

126-5-3-12/31
Study of the Physical Factoi~s whie'l Determizie -the Hardening of
Alloyed Iron
influences to a considerable extent the Uypo Il distortions
(non-unifoi-m mirro-stresses) in deforiaed as as in
hardened alloys. A correspondence exists betvcon the
mabilitude of these type II distortions auld the otren,,th
-values of alloys in Wto hardened state.
3. High degrees of plastic defor:jation brinG about
considerable type III distortions. In the investi.ated
solid solutions considerable displacements of the atoms
take place in alloys in the annealed state,which is caused
byr~ho presence in the atom lattice of lVed elements;
Vu- varied between 0.053 -md C.120 beirW~ the
cm cm
maCnitudo of the static displacements of the aLoils). After
deformation with a hirrh der,ree of reduction in the cold
0
state (filiriGs) the magnitude of increased approxiiuately
to the sari.,,e level (about 0.100 -to 0.120), which is near to
the level of type III distortions in cold deformed non-
alloyed iron. The hiSher the value of a for the
FT, ~Cm_, M
Card 5/9"equilibriLL7111 solid solution, the smaller was the chanrre
Q

126-5-3-12/31
Stud,y of the Physical Factors which Determine the Hardening of
Alloyed Iron
11, this ,-1a:-r1.it%ude as a result of tlio defor:.,_~fion.
4. After hardeninG of the alloyed iron to mnrtensite,
L-1, , -lic il U -
in----nitude of t -,~ static dicnlacenients did no' increase.
Thu.,21 In 4--illoys hardened b,,, -,Le-,ns of tic transforna-
Lion no t.-rpe III distortioilS Occur, ,.lthou~,!-l tht) -trenGth
approach those of materizals deforned in the
Cold L;tate. This could be seen particularly clearly on
s-aecimens of pure iron,hardened to produce ~;artensite.
lio '11-ypo III distortions vieve detected and Larden-inG block
sizes :,rd type II distortions viei' -e on the sc-uae levei as in
case of iron deformed in IV-he col(I state. Consequently,
prosonce oC type III distort~icns a~; least of a nzi~;nitude
dt3toctod in iaeasu_reme.rits, b~ viez,ns of lntcr_:~ive, X-rays is
not a necessarv condition for olutainiiij~ a hiLji resistance
to defo-rimation.
5. Investigation of -the fine cvystalline structure as a
function of the degree of plastic deforination carried out on
pure iron and on some solid solutions has shown that with
increasinC degree of defor:mation the hardness 7 the type II
U
Card and type III distortions increase, ,ihilst the sizes of the
6/9

126-5-3-12/31
Study of the Physical Factors which Deter-nine the Hardening of
Alloyed Iron
blocks decrease. Theze characteriStics change most
rapidly for low degrees of deformation; for deformations
of 30 to 70% -lie chanf~;e of these characteristics is slow.
For hi6her degrees of deformation the speed of the chan6e
in the characteristics increases aGain. The behaviour of
the metal in the case of very high degrees of plastic
deformation requires further detailed investigation.
6. The obtained rersulLsl ,permit the conclusion that
brealrinS up of the re6iono of coherent scattering is a
neccs~;ary condition for dncreasinz.:, the resistance to
deformation of the metals (in the care of the "sliding"
mechanis,m of plastic deformation). The differences in
the absolute magnitudes of the characteristics of the
resistance to deformation. for various inetals and solid
-solutions is due mainly to the differino properties of
the crystals in the micro and sub-micro re~Lions
(character and fcrce of the bond, static eistortions and
other deviations from the regular periodicity of the
lattice) and not by changes in the size of tu'riese regions.
Card 7/9 The established correspondence betyieen the resistance to

126-5-3-12/31
Study of the Phyf;.i-cal Factorv~ .-ihicli Deteimiine the llardenir*~, of
Alloyed Iron
defoi,,-Aation and the LaaGniitude of type 11 dis"Gortions
should not be taken as an indication of the major role
of distortions from the --,)oint of view, of li-irdening.
It be as-suMed tliat, t1jo of tho.~~c -alotortions
elastic deforit:1'at-'i.01s of the 11,lic ro -ro ~,'i oils)
is lts~,,lf due to the propertie., of t1io cr '-~stallit~.~s of
Wic Liven naterial. From th--;-- -DoinL of view th,_-
of `Gype II distortiori,_, sorves ac ail ev--aluation
of the limit of elastic defor_-_~tion of -the micro-reE-ions
and can be considered as beinE; a definite charccteristic
of the properties of the cryctualliteo of a j~iven substance.
It i,- al-o possible that the obsz)rved type II distor-tions
influonce the resistance to deformation causinL; In
increase in the dogree of deorientation of the 'blocks.
The experimental data obtained in the here described work
on the relation betweon the fine structure and the
4
stren,,,,th of a material permit establishin.Z ceru-ain
relations boverniz6 these phenomena and leads to a number
Card 8/9 of new problems, the elucidation of %-.-hich by further
experiments is important from the point of view of

126-5-3-12/31
Study of the Physical Factors which Determine tho Hardening of
Alloyed Iron
understandin6 the nature of c3trcnE;th tmd hardeningr (work
hardeninG) of metals and alloys.
There are 6 figures 6 tables and 33 references,
29 of which are Soviet, 9 English.
ASSOCIATION: Institut metallovedeniya i fiziki metallov (TsNIIChM)
(Institute of Metallography and Metal Physics
TsNIIChM)
SUBMITTED: December 4, 1956
1. Iron alloys--Ifard6ning 2. Iron alloys--Pliysical properties
3. Iron alloys--X-ray analysis 4. Irorv alloys--Crystal structure
Card 9/9

Miaksimova., 0'P,,, INLkoric;rova, A.
Pavlenkol Z. D,)and Yampollskly, A., Ja~
TITLE- Influence of Preliminary Plastic Deformation on the
Mlartensitic Transformation in the Alloy Fe-Cr-Ni
(Vliyaniye predvaritellnoy pla-sticheskoy deforruatsii
na martensitnoye prevrashcheniye v splave Fe-Cr-Ni)
PERIODICAL: Fizika Metallov i Metallovedeniye, 191)8,. Vol 6. Nr 1,
Pp 95-105 (USSR)
ABSTRACT: The results are described of experiments carried out for
elucidating the finer features of the influence of plastic
deformation and subsequent annealinr, on the martensite
transformation in Fe-Cr-Ni alloys of the type Khl8N8.
The aim was to establish the activating effect of
deformation in such an alloy and to verify the validity
of the assumption of the activating influence of stresses
on the martensitic transformation of deformed austenite,
For this it was necessary to study the character of
elimination of the after effects of deformation with
gradually increasing annealin6~ temperature; in view of
the possible super-position of diflusion processes onto
Card 1/8 the processes of stress elimination during annealJng,

:3011/126-6-1-12/73
Influence of Preliminary Plastic Deformation on the "!a.-t(.:,nsitic
Transformation in the Alloy Fe-Cr-Ni
such investigations could not be effected on steel-
If the asSIUMUtiOn on the favotmable influence of stresses
oa the martensitic transformation of deformed austenite
would be correct, the effect of activation should be
eli-ainated in the case of heating in the rT-7e of
relativaly low temperatures. Another a4m of the
described work was to study the influence of deformation
on the isothermal martensitic transforrilition for the
purposo of clucidating the ell arac teri.,7tic featurjs of
the changes in the kinetics coused by -ulae influence. of
the activating and/or the brakin6 effe~;ts of deformation,
Since the activating -n4-'luence of deformatior-, czal only
-- 4' u
be defected iA alloys witU high elasticity values. it
was decided to carry out the experiments an the- alloy
Xh18N8 (0,03% C9 18.10% Cr, 8~1% M) and 'uhc alloy
Kh1?N9 (0.0_5% C5 17,25% Cr, 9,16% Ni), both of which are
similar in composition and as re:,,,ards the martensitic
point, On the alloy Khl8N8 the influence, of deformation
and subsequent heatinC for obtaininE,: marte.-Icitic
transformation during coolini~ was studii)UJ , whilst on the
Card 2/8 alloy Khl7Vq the influence of deformation on tile isotilk"I'l-al

"OV/ 1. 2r- -6- 1- 12/ 3 3
4.
influence of Preliminary Plastic Deformation in Lhe MarUenilitic,
Transfonaation In the Alloy Fe-Cr-Ni
martensitic transformation was studied,, Investigations
were carried out on flat 3,,5 x 5,5 x 25,5 MM specimens
which after manufacture were subJected to diffusion
annealing at 1150 C for ten hours, The plastic deforma-
tion was effected by compression by irriegns of a press
at room temperature,,, at 100 and at 175 C. Deformation
at 100 and 175 C was effected- inside a special sleeve
fitted with a heater wjndinE ; as, a medium for ensuring
the temperature of 0100 C boiling water was used, whilst
deformation at 175 C was effected in glycerine,
Evaluation of the change of the ability of the austenite
to become transformed Into martensi-11--le was effected by
moans of the thermo-magne Ic method by plotting the 0
cu.rv(.s of cooling ~o -196 C and subsequent heating to 20 C
with a speed of 10 C/min, As the basic criterion of the
stalMity of the austenite, the total effect
was chosen which was obtained as a result of coolin6 and
he,atinS, The change in the fine structure of the
austenite during the plartic defori-lation and durin6 the-
Card 3/8 subsequent heatiri,,- vias investiLated by the X-ray method

SOV/12G-6-1-12/33
Influence of Preliminai-y Flastic Deformat-ion or). the
Transformation in the Alloy Fe--Cr-Ni
by iaeasurinr, the- width of the line (~11),, As a
characteristic of the state of the structure of the
austenite (-Type II stresses dimensions of the blocz'ks
and coherent scatterini~), the -iiagnitude of physical
wideiiing cf the (511) aust~!nito lineL; wLs ,hoc&rj, In
Fi,:-,l t1le traiisformati -i qf the austenite ln~o
8 U
U j. ng
durinE cooling to -1% C and subsequent heaT to
i-- eraphed E,fter va,,ious degrees Of 1)1,:i1-'31-,",~.
defor;-,.iotion at E-oom te;aperaturo for 1--h1c. alloF Ydilbii8~,
in FiC.-,2 the sajae relabion is Sr,~phed for the Case Of
deform.-Lions takiri~- Okoce at, '100,C a iid a ~, 1'7'~0 1 n
FI-I,-,r) 1,111-C oh;lrl~se ')A* the tot.11 ,fl'.-ct of
trMMf0T'Mz1t.1Q,L ac a Suactiol) Uf -It",t, of
plustic defomatioi-, 11s, graphed for va-!:-'Dus
of prodiiidiv-U-y ulie A.Ioy KhL"~N,i, III
Fit,,4 the influence of t1o.) ,Anne~.klj.116 tei!iperatur,o 01"
.L I- -~ ;-ooli!ib
transformation of the de'oriaed austenite dl,-in, -
to -1960C and heat-ing -to 20(c is vraulled for Various
0 ;~.) .
degrees of deformation at 100 C (allo ,7 K h IS'll i In Fig,.5
Card 4/8 fhe change Of the viideulii~s of L-he lhl(~ (311) the

'30 V/ 1 3
Influence of Preliminary Plastic Deformation on th-.e 11a.-tensitic
Transformation in the Alloy Fe-Cr-Ni
austenite, of the total effect of martensitic transforma-
tion (during cooling and during heating) and the ch~~nge
of the martensitic point are graphed as functions of the
annealing temperature gor specimens of the Kh18118 alloy
deformed by 10% at 100 C. In Fig.6 the temperature
dependence of the initial speed and the total effect of
isothermal martensitic transformation are graphed for
non-deformed and deformed (8 aBd 17%) states for a
deformation temperature of 100 C (alloy Khl7r,9), It was
found that, depending on the conditions of deformation
and annealing, plastic deformation can have an activating
or a braking effect on the martensitic transformation',
Small degrees of deformation activate the transformation,
i.e., widen the te aperature range of the transforniation..
bring about an increase of the initial oreed of the
isother..,ial transformation and of the total quantity of
the martensitic phase., Various chaii6es in the fine
crystalline structure of the austenite may lead either
to easier formlation of martonsito nuclel durin,, subsequent
Card 5/8cooling or may impede their formation, For small degrees

SoV/126-6-1-12/3z
.ar
Influence of Preliminary Plastic Deformation on the tensitic
Transformation in the Alloy Fe-Cr-Ni
of plastic deformation those structural chant~es !aill
occur to an increasin6 extent which brint~ aboat the
formation of geiTiinations. However, ever at such
deUrees of cleformntion chanfw-es occii-r- in the ai-istenite
which impede t-raiisformation, With incrcnsJnj~ dp,~Sree of
defoi-mation and also with lncreaEln.: defor!iiabion
temperature, the changes in the structure which bring
about brr,.king of the tran-sforiuttioris increase in
importance, The ohan(~a3iri the flne cr~,strtlilno
structure, vAiLch activate the transforiiationare elimimated
at relatively low annl~alin:-' temper-,atures which t-he
width of interference linas does not yet chanEe, i.,e, whil-sr,
there are still no important changes ir. the manitlide of
the Type II distortions or in the dimensions of the
areas of coherent scatterin,,-, Changes In the structure
braking the formation of germinaLions,=e ,.iaintained
thereby; elimination of these takes place only at higb.er
temperatures corresponding to the region of decrease in
the degree of blurring of the lines, It is not possible
Card 6/8 as yet to establish those details of the fine structure
"-4

SOV/126-6-1-12/33
Influence of Preliminary Plastic Deformation on the Martensitic
Transformation in the Alloy Fe-Cr-Ni
which favour the formation of martensite germinations and
those which impede their formation. Comparison of the
results relating to the influence of plastic deformation
on the inartensitic transformation in Fe-NI-Mn and
Fe-Cr-,Ni systems leads to the conclusion that the intensity
of the deformation caused changes of structural factors
depends on the elastic-plautic properties of the austenite,
The relation between the changes bringing about activation
and braking of the martensitic transformations may differ
depending not only on the degree of deformation but also
on the elastic-plastic properties of the initial phase,
As a result of this an unequal character of the effects
of plastic deformation on the martensitic transformation
Card 7/8

SOV/126-6-1-12/33
Influence of Preliminar7 Plastic Deformation on the "artensitic
U
Transformation in the Alloy Fe-Cr-Ni
was observed in various materials.
There are 6 figures and 11 references, 9 of which are
Soviet. 1 German, I Eni~lish'~
ASSOCIATIOR: Tsentrallnyy naucb-no-issledovatellskiy institut
chernoy metallurgii. (The Central Research rhWtutS Of
Fer"us Metallurgy)
SUBMITTED: I'larch Ll, 1957
Card 8/8 1. Chromium-1ron-nickel alloyn--Trancforniatlons 2.
iron-nickel alloyLi--Deformation 3.
alloyo--ifeat tre&trrent

18(4,7); 25(l) PHASE I BOOK EXPLOITATION SOV/2306
Akademiya nauk Ukrainskoy SSR. Institut metallofiziki
Voprosy fiziki metallov i metallovedeniya (Problems in the Physics
of Metals and Metallography) Kiyev, Izda-vo AN Ukrainskly SSR,
1959. (Series: Its: Sbornik nauchnykh rabot, Nr 9) Errata
slip Inserted. 3,000 copies printed.
Ed. of Publishing House: V.L. Shkurko; Tech. Ed.: M.I. Yefimova;
Editorial Board: V.N. Svechnikov, Academician, Academy of Sciences,
Ukrainian SSR (Reap. Ed.); S.D. Gertsriken, Doctor of Physical
and Mathematical Sciences; and I.Ya. Dekhtyar, Doctor of
Technical Sciences.
PURPOSE: This collection of articles Is intended for scientific
workers, aspirants, and engineers in the fields of the physics
of metals., metallography, and metallurgy. It may also be useful
to students of advanced courses in metallurgical and physical
faculties.
COVERAGE: This collection of articles dea13 with the following
Card 11,12-

Problems in the Physics of Metals (Cont.) SOV/23o6
topics: effect of high-speed heating, heat treatment, deforma-
tions) and crystallization conditions oil phase transformations,
structures, and properties of metals and alloys; the effect of
additional alloying components on volumc-L'ric and Intercry3talline
diffusion In alloys; and the effect of repeated quench hardenlng
and radioactive and ultrasonic treatment on the physical proper-
--ties of alloys. No personalities are mentioned. References
follow several-6f the articles.
TABLE OF CONTENTS:
Kurdyumov, G.V., and L.G. Khandros. TranS41 ormation of Fine
P-a-r-El-cl-esof Fe-Ni.~-Alloys to Martensite 3
Transformations of filings of two alloys (33 percent Ni.
and 28.6 percent Ni) annealed in quartz ampoules were
studied.
Khandros, L.G. Changes in the Austenitic State of Manga-
nese Steel During Transformation to Martensite 7
Card 2/3-12

VITMAN, F.F., prof-, doktor fiz.-mat.nauk, oty.red.; OFFS, A.F., akademiki
Yed.;-_XUUTUMOV. G.V , 6kademik, red.1 ZHURKOY, S.N., red..-
KONSTANTiNdf.-B.-P., -;;d.-, GLIKKAV, L.A., prof., doktIoIr tekhn.
nauk, rod.; 2LATIN, N.A., doktor fiz,-mat.nauk, red.; SWAROV,
..V:A:.'v doktor takhn.nauk. red.; FRIDMAN, Ya.B., prof., doktor
tekhn.nauk, red.; IOWE, B.S., kand.tekhn.nauk, red.; AVIRITANOV.
V.I., rod.izd-va; PEVZNER, R.S., takhn.red.
[Some problems on the strength of solid bodies; collection of
articles dedicated to the 80th birthday of N.N.Davideakov, member
of the Academy of Sciences of the Ukrainian S.S.R.) Nekotorys
problemy prochnosti tvardogo tala; obornik statei, pneviashchennyi
vosimidesiatilatiiu akndemika AN USSR N.N.Davidenkova. Moskva,
1959. 386 p. .1 1. (MIRA 12:6)
1. Akadsmiya nauk SSSIL 2. Chlen-korraspondent AN SSSR (for
Zhurkov, Konstantinov).
(Strength of materials)

~_KMYUKOVA GJ., okademik, obahchiy red.; NOVIKOV, I.I., o'bahchiX r-3d.;
~-Iimiy' S.V., kand.med.nauk, red.; FRUSAKOV, V.N., 11-Aud.kbim.
nauk, red.; SXDOV, V.V., kand.med.nauk, red.; ANIRMYENKO. Z.D.,
red.; KAZIMI, Ye.I., tekhn.red.
LProcoodings of the Second International Confefence on the Peace-
ful Uses of Atomic Energy, Geneva, 19581 Trudy Vtoroi me2hdu-
aarodnoy konferenteii po mirnomu ispollsovaniyuntomnoy energii.
Zhoneve, 1958. (Doklady sovetskikh uchenykh) Moskva, Izd-vo
Glav.uprav. PO ispO1120VOnAW atomnoy energii pri Sovate Hinistrov
SSSR. Voi.6. (Production and application of isotopes] Poluchenie
i primenenie izotopov. 1959. 388 p. (MIRA 12:11)
1. International Conference on the Peaceful Uses of Atomic Energy,
2d, Geneva, 1958. 2. Chlen-korrespondent AN 55SR (for Novikov).
(Isotopes)
t M-

,.-KURMUMCVt G.V., akademik, red.; SINITSYN, V.I., red.; PANASMKOVA, Te.I., red.;
MAZHL4-rYe.Lv tekbn, red,
[Transactions. Selected reports by foreign scientists] Trudy. [Izbran-
rqe doklady inostramVkh uchorWkhj MosWa, Izd-vo Glav. uprav. p0 ispoll-
zovaniiu atomnoi energ. pri sovete Ministrav SSSR. Vol.10. [Production
and use of Isotopes] Polucbenie I primenenie izotopov. Pod obshchei red,
G.VAurdiumova. 1959. 603 p. (MIRA IAM
1. Vtoraya mezbdunarodnaya konferentsiya po mirnowu ispollzovaniyu atom-
noy energiip Zhenevaj 1958. (Radioisotopes)
49

BILIDZYUKETICIT, !.A.; KURLMMOV, G.V.; MIMROS, L.G.
Aging of certain Iron-nickel-chrrmium baso hent-rosiBtant
alloys. Issl.po zhurapr.oplav. 4:208-213 '59.
(HIU 13:5)
(Heat-rouistant alloys)
(Iron-nickol-chromiun alloys)

I
160) SOV/48-23-5-16/31
AUTHORS: Zasimchuk, Te. E., Kurdyumovi 0. Vo, Larikov, L. N.
TITLE: The Influence of Alloy Elements on the Kinetics of Recrystal-
lization. of the Alloys With Nickel Basis (Vliyaniye legi-
ruyushchikh elementov na kinetiku rekristallizatsii splavov
na nikelevoy osnove)
PERIODICAL: Izves*ljiya Akademli nauk SSSR. Seriya fizichaskayat 1959j
Vol 23, TIr 5, pp 615-619 (USSR)
ABSTRACT: The introduction to the present paper contains a table
accurately describing ihe analyses of 27 alloys. Each of
these alloys was converte'd to the monophase condition by
thermal treatment and subsequently deformed at room tempera-
ture up to 80%. The samples were then annealed from 5 minutes
to 10 hours in the temperalure range of 280-900 OC, and the
state of recrystallization was investigated. The time was
measured after which the primary center of recrystallization
attained the magnitude of 10- cm at a given temperature. The
results obtained from various measurements of the alloys in
question are summarized in four diagrams; the logarithm of
time T, elapsing unttl the appearance and growing of the
Card 1/2 first recrystallization centers up to a magnitude of jo-3cm)

SOV/48-23-5-16/31
The Influence of Alloy Elements on the Kinetics of Rocrystallization of
the Alloys With Nickel Basis
is plotted on the ordinate, and the value T-1.103 is plottea
on the abscissa, with T egualling the absolute annealing ter.-
peraturo'. It holds -r - Ae RT , i.e. the measuring values of
each individual alloy lie on a straight line, each alloy
possessing its own characteristics. The energy activating
reorystallization is determinod from the velocity at which
recrystallization takes place. These values are summarized in
t&ble 2 and are indicated in kcal/g-atom. Two further diagrams
(Figs 5, 6) show the values of the activating energy, of the
diffusion coefficient and of the modulus of elasticity of
nickel alloys with chromium and molybdenum. Finally, conclu-
siona are drawn from the results concerning tbe nobility of
the atoms in the metal lattice, the concentration ratios in
the boundaries of the growing recrystallization centers, and
concerning the dependence of the surface tension on concentra-
tion. There are 6 figures, 2 tables, and 11 references, 9 of
which are Soviet.
ASSOCIATION: Institut metallofiziki Akademii nauk USSR (Institute of Metal
Card 2/2 Physics of iha Academy of Sciences, UkrSSR)

18(4),18(6)
AUTHORS: Academician, SOV/20-124-1-21/69
Kritskaya, V. K., Latayko, P. A., Osiplyan, Yi. A.
TITLE: On the Variation of the Forces of Interatomic Bond in a
Single-phase Solid Solution Nickel-aluminum (Ob izmenenVakh
ail mezhatomnoy svirazi v odnofannom tverdom rastvore nikell-
alyuminiy)
PERIODICAL: Doklady Akademii nauk SSSR, 1959, Vol 124, Tvir 1, PP 76-78
(USSR)
ABSTRACT: Short reference is first made to earlier papers dealing w1th
this subject. The castings of the nickel-aluminum alloy
(8-3 atomic e,* Al) were annealed for 100 hours at 1,1500 '21rhe
forging of the casting up toa cross section of 40 x 25 mm
began at 1fOOOo and was completed at a temperature of
- 400-5000. Towards the end of the forging process the
casting had already assumed a dark color. The forged work.-
pieces were then cold-drawn and from them samples of 100 trim
length and 10 mm diameter were produced. On these samples,
Young's modulus was determined by measurement of the
resonance freqaencioa in the case of longitudinal oscillations
Card 1/3 of the rod at room temperature. The results obtained by these

On the Variation of the Forces of Interatomic Bond SOV/20-124-1-21/69
in a Single-phase Solid Solution Nickel-aluminum
measurements are shown by a diagram for various initial alloy
states. In the cold deformed and in the hardened state
Young's modulus of the alloy is higher by 6 43 than in the case
of an annealed alloy..In order to convey the alloy from a
state with a high modulus (state B) into one of a low
modulus (state A) it is necessary to heat it up to temper,-Aur-
es of more than 600-7000, after which it is gradually cooled
down. With heating up to 700-1,0000, Young's modulus gradually
decreases. For the purpose of conveying the alloy from state
A into state B it is sufficient to heat up to 3000 with sub-
sequent cooling in water. Already after heating up to 1000
the modulus is noticeably increaned. The state A does not 0
change if cooling takes place slowly after heating to 300
or higher temperatures. These data make it possible to draw
the conclusion that state B in a hardened alloy is not
produced by undercooling of a steady state at high temperatur-
es down to room temperature, but rather by such a tranaforma-
tion which occurs in the alloy only in the case of rapid
cooling within the temperature interval of from 3000 and
Card 2/3 room temperature. If the alloy is heated in state A up to
.M

On the Variation of the Forces of Interatomic Bond SOV/20-124-1-21/69
in a Single-phase Solid Solution Nickel-aluminum
3000, no essential changes occur in it either during heating
or during aging. A change occurs only during rapid cooling.
Prom the data discussed it further follows that the state B,
which is produced by the rapid cooling of the alloy at a
temperature below 3000, is a metastable state, which, in the
case of a sufficiently high temperature, i.e. in the case of
sufficient atomic mobility, may go over into the stable state
A. At present, the nature of the alloys with high Young's
modulus and the nature of the transition A -) B is not yet
known. The Debye X-ray pictures showed no difference between
the crystal structures of the alloy in -the states A and B.
However, an essential difference was observed with respect to
the microstructure of the alloy. Similar results were obtained
also for a solid'solution Ni - Cu (10.6 atom ~',' Cu). There are
3 figures and 8 references, 5 of which are Soviet.
SUBMITTED: September 26, 1958
Card 3/3
"A

4 66453
JD
, P,.
- %
AUTHORSt Kritskaya, V. K., V,, SOV/20-129-3-21/70
Academician, Osiplyan, Yu. A.
TITLEt On the Nature of the Variations of Young's Modulus in the
Thermal Treatment of Single-phase Alloys on the Basis of Nickel
PERIODICAL: Doklady Akademii nauk 33SR, 1959, Vol 129p Nr 3y PP 550-552 (USSR)
ABSTRACTt The present paper investigates the dependence of the elastic
modulus on thermal treatment carried out on samples of pure
nickel (electrolytic nickel twice remelted in a vacuum) and on
some solid solutions on a nickel basis (Ni + 10~ Cu, Ni + 10% Co,
Ni + 3-5% Mo). All these alloys were single-phased during the
entire interval of the heat treatment. Both in the case of nickel
and in all alloys investigated, the variations of the elastic
modulus depend on the manner in which they are cooled down from
high temperatures. The dependence of the elastic modulus an the
temperature of thermal treatment is shown in a diagram. For
nickel and for all solid solutions this dependence is qualitaltiveJ~y
the samei it is similar to the dependence for the alloy Ni-Al.
The differences between the values of the elastic modulus in the
state A (with a low value of the elastic modulus) and the state B
Card 1/3 (wi1h ahigh value of the elastic modulus) fluctuate between 91A for

664,53
On the Nature of the Variations of Young's Modulus in SOV/20-129-3-21/70
the Thermal Treatment of Single-phase Alloys on the Basis of Nickel
0
nickel and 12% for the alloy Ni -- Co. A microstructure with many
lines of slide is characteristic of the state B. A vertical
displacement along the individuaJ. slide lines could be observed
in the interference microscope, in the states A and B the
investigated alloys have not only different values of the elastic
modulus at room temperature, but also a different temperature
dependence of the elastic modulus. For the annealed samples
(state A) the temperature dependence of the elastic modulue has
an anomalous character within the temperature interval of from
room temperature to Curie point and is represented by means of a
curve with a minimum. After quenching from a temperature that is
higher than that of the tOttLl transition A 4 B, this
anomaly of the elastic modulus vanishes, and in the state B
it decreases in a monotonic manner with increasing temperature
in the case of all alloys. After quenching and annealing, the
difference between the values of the elastic modulus of
nickel and its solid alloys is not determined by the
difference in the strength of the binding forces, but by the
influence exerted by the structure upon the mochanostrictional-,
Card 2/3 i7

66453
On the Nature of the Variations of Young's Modulus in the SOV/20-129-3-21/70
Thermal Treatment of Single-phase Alloys on the Basis of Nickel
deformation of the ferromagnetic samples. The streaaes
leading to sliding in the case of rapid cooling are not due to
a magnetic tranaformation during cooling. There are
4 figures and 4 references, 2 of which are Soviet.
SUBMITTED: Augue~ 3. 1959
Card 3/3

SOV/126- --7-5-18/25
AUTHORS: Perkas, M. D. and Khandron, L. G,
.2v P G - I. ,
TITLE: On the Role Played by Secondary Distortions in the Hardening
of Metals (0 roli iskazheniy vtorogo rods. v uprochnonii
metallov)
PERIODICAL: Fizika metallov i metallovedeniye, Vol 7, Nr 5, pp 747-,7bl
(USSR)
ABSTRACT: In this paper binary Fe-Ni alloys containing 10., 25 and
28% nickel were investigated. The specimens were quenched
from 1000 - 10500C and gubsequently tempered in the
temDerature range 100-550 C for I hour. The alloy containing
25~'Ni was particularly thoroughly investigated. Hardening
by quenching resulls in considerable secondary distortions
(As/& Z 2,8 x 10- ), the magnitude of which is close to that
obtained in quenched steel containing 0.1% carbon (age Ref.9).
The mosaic blocks are broken up to a size of 3 x 10-u cm, and
the ultimate tensile stress ( 0-s) and hardness (EV) are
80 kg/mm:2 and 265 VFN, respeotively. Subsequent tempering
Card at 3000C brines about a decrease in the secondary distortion
115 (from 2.8 x 10-6 1.9 x 10-3~jc but the remain ng prop-
erties D, HVJ o-Y remain prac ally unaltered Isee Fig.1).

j'0 V.11
On the Role Played by Secondary Distortions in the Hardening of Metals.
Heating the specimens to higher temperatures loads to a further
decrease in tiecondary distortions, and after tempering at
4500C Aa/a is 0.3 x, 10-3. After such tempering the
hardness and UTS remain practically unaltered, but the block
SiZ8 tends to increase. On heating the specLuens to above
460 0 the reverse transformation ve -> takes place, and
therefore after cooling to room temperatle the microstrueturo
contains the y-phaso together with the oc -phase This
Y -phase possesses an increased resistance to
transformation to martansite on subsequent oooling. In this
connection a study of sgeolmens of this alloy, tempered at
temperatures above 460 C, was inexpedient. An attempt was
made to attain at least some softening of the Fo *25% Ni
alloy by lengthy soaking of the specimens at a temperature
somewhat lower than the beginning of the ty I transform-
ation. The specimen was tempered at 4400C fol 70 hours.
The axp9rimontal results, howgvor,, have shown that the hardness
Card and the widths of interference lines were close to those
2/5 obtained after 1 hourla tempering at 4500C. In the Fe t 10% X
alloy the reverse cK-> -~ transfomation begins at approxi--

SOV1126-
On the Role Played by Secondary Distortions in the Hardening of Metala
mately 60000. Therefore the quenched specimens oan be
tempered at least up to 550-5800C without running the risk
of y-phase formation. Data on the change of the fine etruoturs
and'hardness of this alloy are shown in Fig.2. The extent of
secondary distortions in a 10% Ni alloy changes little after
tempering at 3000C, but a considerable decrease in seeondary
distortions occurs in a temperature range above 30000. On
tempering at above 4500C an increase in block size and some
decrease in hardness is observed. For an Fe + 28% Ni alloy
the nature of the change in hardness and fine structure on
tempering was the same as in the case of the 25% Ni alloy.
In order to elucidate the role played by sooondary distortions
in the hardening of alloyed iron the following experiments
were also carried out with a quenched specimen of the 25%
nickel alloy. The alloy hardened bX quenching exhibited the
following values: Aa/a x 2.8 x 10-0., D a 2#8 x 10*'9 am and
EV w 260 (see Figol). Aftor tempering at 40000 for 1 hour
the hardness and block size were practioallyunaWrid and the
secondary distortions had decreased to 0.7 10 Fig.1).
Card The speolmen was then given a cold plastic deformation with a
3/5 summary reduction in area of 60%. After deformation th
secondary distortions had again increased from 0.7 x 10-S

SOV/126- -7-5
On the Role Played by Secondary Distortions in uie Hardeuing of Metala
to 2.0 x 10-3. The block size and hardness were 2,9 x 10-6
cm and 270 E respectiv 1 1 e. they had remained at the
same level (s~ e Table P.7ZOT! ;he other specimens of the
same alloy wom tempered at 4500S af ter quenching. After
tempering, bAla was 0.3 x 10- , D - 3.5 x 10- and HV -
265. As a result of a subsequent cold lastio deformation
with a summary reduction in area of 60 the secondary
distortions had increased to 2.9 x 10-~ whilst block size
and hardness had again changed comparatively little (D a 2.8 x
10-6 cm and H = 283. Thus the available data on the
relationship beyween hardness and fine crystal structure of
met--is and solid solutions enables one to conclude that the
most important crystal structure factors determining the
hardness of metals and one-phase alloylart, breaking down
of the grain size to fragments of 10 -0- cm with a con-
Card sideriLble disarientatlon or the lattloo between the rragmeatab
4/5 and the formatioN within the fragmentpof a sub-microsoopic
block struoture.

SOM 2116.
On the Role Played by Secondary Distortions in the Hardening of Metals
There are 2 figurev, I table and 9 Soviet- references.
ASSOCIATIOW: Institut metallovedeniya i fiziki metalloT TsNIIChM,
Institut metallofiziki AN USSR (Institute of Metallurgy and
Physios of Metals TsNIICbM, Institute of Metal Physica,
Ao. So. , Ukrainian SSR)
SUBMITTED: January 22, '1959
Mard 5/5
p~-;l -A-

SO
AUTHURS: Kardonskiy, V. M., Kurdytg1ov,_Q.)~. ana Perkas, M. D,
TITLE; Influence of the Properties of Crystals on the Strength of
Metals In the Hardened Condition (0 vliyanil 3VOYStY
.kristallov na prochnost' metallov Y uprochnennom sostoyanil)
PERIODICAL: Fizika metallov 1. metalloyedeniye, Vol 7, Nr "V, pp "b2-7bf~
(USSR)
ABSTRACT: Kurdyumov et ali! (Ref92) hsLye shown that there exists a
linear relationship between the degree of secondary distortion
and the hardness of marteasite in quenched low G steels (see
Pig.1). Golubkoy et alil (Ref.3) have shown that there
existo a direct relationship between the degree of secondary
distortion and the hardness of alloyed iron after cold plastio
deformation (see Pig.2)~ Using results obtained b thq
latter authors a diagram has been eonstruoted (Pig.3~ nhowing
the dependence of the degree of secondary distorticr-, arising
as a result of cold plastic deformation, on the hardness of
the original azuiealed alloy iron. Prom the above diagram it
Card can be seen that the absolute hardness of hardened alloys is
1/1t. determined not only by the fine grain structure but also by

Influence of the Properties of Crystals on the SLrength of' Metais In
the Hardened Condi6ion
the properties of the crystals of the original metals as
annealed. These propertiez also determine the elastlz iimit-
of micro-.regions, A&/a, in the hardened state. For a
further study of the above conclusions the authors invest-16atsd
alloys in which the properties of solid solution orystuls
strongly depended on the conQentration of the dissolyed elements.
Among the Iron alloys the most suitable ones for Izvesti6ation
are Iron-aii1con alloys with a silicon content up to thq
limiting solid solubility 11-i c\-Alron,, The chemit-al composition
of the original 'iron and its alloys with siiicun Is given 1u
Table 1. The methods used for flie study were the 3amg as
those employed by Golubkov et alli (Ref.3). In Table 2 the
results of hardness, UTS and temporary resistanco measwoment.3
of annealed alloys are shown. In Fig.3 curves are plotted
which express the dependence of hardness on the degree of
plastic deformation. The relatiu.-aship between the strength
Ca,rd p - o p 9 r t 19 a and the fine structure in the hardened state
2/4 Were studied In specimens of alloys which had been deformed at
identical loads (85 tons). The degree of deformation wa5
found to Tary from 68% for iron free from aillcon to 48%

OSOV1126- - --7-5-
Influence of the Properties of Crystals on the SLrength of Metals in
the Hardened Condition
fqr an alloy containing 9.4% Si. In accordance with tho
results shown 11 in Fig.4 the hardening of all the alloys must
be close to saturation". The results of the study of the
specimens are shown in Fig.5. These show that the
incroase in hardness as a result of cold deformation is not
related to the magnitude of secondary distortions arising
during deformation as it is practically independent of the Si
concentration, whilst Aa/a Increases by nearly twice.
However, Aa/a increases proportionately to the hardness
of the annealed material. Thus the results obtained are in
agreement with the idea that the secondary distortions are
not alone responsible for the hardness arising from the oold
deformation and martensite transformation, but reflect the
properties of crystals of a given material, characterizing
the "limit" of the elastic deformation of nAcro-regions.
These properties determine the level of the strength which
Card can be attained as a result of changes in the internal
3/4 microscopic and sub-microseopio grain structure In the
hardening process.

SOV11126-
Influence of the Properties of Crystala on thG itrangth of Metals ia
the Hardened Condition
5 f4
There are &gures, tablos and 7 references, of which 6
are Soviet and 1 1~ngllsh.
ASSOCIATIOVi Institut, mazallovedenlya I fiziki metalloy TaNIIChk
(Institute of MetallurEy and Metal. Physics TsN11ChM)
SUBMITTED: January 22, 1959
Ca-.,,d V4

"c; RABINOVICH, A.M., red.; LEVIT,
TO.I., red,izd-ve; DORUZHI#_:kAT.4, L.Y.. tekhn.red.
[Phenomena of the hardening and tampering of steel] IAvlaniia
zakalki i otpuoka stall. Kookvas Goa.nauchno-takhn.izd-vo lit-ry
po chernoi i tavetnoi metallurgii, 1960. 63 p. (MM 14:2)
(Steel--Heat treatment)

5/129/60/000/010/004/009
E193/E483
AUTHOR: Kurdyumov, G.V., Member of the Academy of Sciences USSR
TITLE: ure o he Hardened State of Metals
PERIODICALi Ma-Lallovedeniye i termicheskaya obrabotka metallov,
196o, No.10, pp.22-30
TEXT: The article is the text of a lecture delivered at the
All Union Conference on Theoretical Problems of Metal Treatment,
held in November 1958. Based on previously published results of
various investigations, conducted by the present author and other
workers, the effect of heat and mechanical treatment on the strength
of metals and alloys is discussed. It is pointed out that the
increase in strength of pure metals or single-phase all ys due to
cold plastic deformation or martensitic transformation'ris always
associated with the fragmentation of grains, misalignment of the
sub-graina thus formed and the formation (within the sub-grains)
of blocks\which constitute sub-microscopic regions of coherent
scattering of X-rays. In addition, the actual strength of a
given material will depend on the properties of the crystals of
which the material consists, such as the yield point in the
anneal.ed condition and the magnitude of the distortion of the
Card 1/3

s/i2q/6o/ooo/oio/oo4/ooq
E193/E483
The Nature of the Hardened State of Metals
second type (ela.itic deformation of microscopic dowtains),
caused by heavy plastic deformation or transformations of the
martensitic type. Thus, the first necessary condition for
increasing the strengths of a metal or alloy is the attainment of
uniformly distributed microscopic and sub-microscopic structural
heterogeneity. Fuvthev increase in strength, with the aid of
mechanical or heat treatment, depends on the extent to which the
degi-ee of dispersion of this structural heterogeneity can be
increased and on the possibility of' formation (in the micro-regions
of new phases with higher resistance to deformation. The
possibilities offered in this respect of cold plastic deformation
are limited by the maximum amount of deformation a metal can stand
without fracture or without formation of micro-cracks or their
nuclei. To some extent this difficulty can be overcome by
deforming materials under the conditions of hydrostatic pressure.
Finally, metals characterized by strength approachiAg the
theoretical -value can be obtained by preparation ol' single,
defect-free crystals, the advantage of this method being that it
yields material in a stable condition as opposed to thermally or
Card 2/3

S/129/60/000/010/004/009
E193/E483
The Nature of the Hardened State of Metals
mechanically treated metal which retains its strength only
within a certain temperature range. There are 6 figures,
1 table and 10 Soviet references.
ASSOCIATIONt TsNIIChM
Card 3/3

84684
I'l os" ~s D 9. S/020/60/134/004/008/023
Yq b~WD B019/BO67
AUTHORSs Batenin, I . V., Illina, V. A., Kritskaya, V K,;
.Kurdyumov, GG. V., Academician, and-Ch-arov, IF7-V,

TITLEt Effect of Neutron Irradiation o n the Crystalline' Fine
-
Structure and the Properties of Metals and Alloys
PERIODICkLi Doklady Akademii nauk SSSR, 196 0, Vol. 134, No, 4,
-pp. 602 - 805
TEM The authors studied the broadening of X-ray interference lines qf
(1020 102'
iron, iron alloys, and copper by neutron irradiation ,
Prior to the experiments the samples were annealed at 600 650'C, Fig; I
shows the changes of the (220).- and (400) interference lines of iron and
copper due to neutron irradiation, Fig. 2 shows two X-ray photographs of
copper (before and after irradiation). In Table 1, the changes in the widths
of the interference lines are summarizedt
Card 1/3

Effect of Neutron Irradiation on the S/020/60/134/004/008/023
Crystalline Fine Structure and the Properties B019 B067
of Metals and Alloys
Table 1
Material Indices vf Line w idths Distortions Block dimensions
the reflecting before aftir of II kind 6

surfaces
i;rad.
irrad..
Aa/a.10 3 D~10
cm
Fe (110) 5,.0 5.6 0~65 6
220 7.3 9-4
CU 200
~
~ 5.9 7.0
400
1
1 1110 1 15.6 1 .1 1 5
In Table 2 the changes in microhardness are given, The values are between
26 and 66%, according to material and irradiation intensity~ Since the
changes in the interference lines are the same as in cold-forming, the
autho.es conclude that neutron irradiation leads to a reduction of the
regions of coherent scattering and to microten9ions, as is the case in
cola-forming. The solidification of the material is connected irith the
change in the crystal properties in the microregions Here. the resistance
to dislocations in the lattice is increased, The authors conclude there-
Card 2/3

84684
Effect of Neutron Irradiation on the S/020/60/134/004/008/023
Crystalline Fine Structure and the Properties B019/BO67
of Metals and Alloys
from that the increase in microhardness is summed by irradiation and cold-
forming. This exactly applies for iron,as is shown by the diagrams in
Fig, 2. For the anomalous behavior of an iron tungsten alloy (6% 71) it is
assumed that irradiation not only causes defects of the type "external
atomic vacancies" as is usually the case but also a change in the
distribution of the tungsten atoms in the direction of the thermodynam-
ically more stable state. There are 3 figures, 2 tables, and 6 Soviet
references,
ASSOCIATIONt Inatitut teoreticheskoy i eksperimentallnoy fiziki Akademii
nauk SSSR (Institute of Theoretical and Experimental
Physics of the Academy of Sciences USSR). Institut metallo-
vedeniya i fiziki metallov Tsentrallnogo nauchno-issledova-
tellskogo instituta chernoy metallurgii im., 1, P. Bardina
(Institute of Metallography and Metal Physics of the Central
Scientific Research Institute of Nonferrous Metallurgy imeni
I, P. Bardin)
SUBMITTEDi June 29, 1960
Card 3/3

19-9M
26795
s/i2g/61/000/009/003/oo6
E193/E380
AUTHORS; Kurdyumov, G,V,, Academician of the AS USSR and
-,Candidate of Technical Sciences
TITLE: On the Effect of Crystal Properties and Grain Sub-
structure on the Strength of Metals
PERIODICAL: Metallovedeniye i termicheskaya obrabotka metallov,
1961, No. 9, pp. 33 - 43
TEXT: An analysis is presented of experimental results,
published in recent years both in the Soviet Union and abroad,
with the object of elucidating the basic structural factors
determining the strength of metals. It is shown that although
distortions of the second type (lattice distortions) hardly
affect the resistance of metal to deformation, they characterise
the relative properties of the crystals of a given substance
which, in turn, affect resistance to deformation. The effect of
various mechanical and thermal treatments on hardness, the
-dimensions of blocks and the magnitude of Aa/a in Fe-Si alloys
are discussed as well as the temperature-dependence of the yield
point and UTS of preliminarily quenched and annealed
Card 1/3
M.-

26795
S/129/61/000/009/003/Oo6
On the Effect of Crystals .... E193/E380
apocimens
250,0' Ni-Fe alloyA the temperature-depondence of hardness and the
width of interference lines of Fe and Ni, the effect of cold work
on hardness and dimensions uf the regions of coherent scattering
and the effect of neutron bombardment on microhardness and yield
point of metals. Several conclusions are reached:
1) the resistance of metals to deformation is determined mainly
by the properties of crystals (that is, by the resistance to
movement of dislocations in the interior of sub-boundary-free
regions) and by the grain sub-structure (that is, by the
dimensions of the sub-microscopic domains, the existence of
sub-boundaries, degree of misorientation of adjacent regions,
etc.). The effect of both these factors is additive.
2) The properties of the crystals can be altered by the addition
of alloying elements, by creating distortions in the interior of
sub-microscopic domains (for example, by neutron bombardment
or by quenching of pure metals), and by varying the temperature.
A comparative assessment of the properties of the crystals can
be made by measuring the yield point or hardness of annealed
material, or by determining the magnitude of lattice distortions
Card 2/3

26795
S/129/61/000/009/003/oo6
On the Effect of Crystals E193/E380
in cold-worked specimens.
3) Alloying can bring about a change in the temperature-
dependence of both sub-structure stability and crystal
properties. If alloying is to increase the high-temperature
streneth of a metal, both factors must be changed in the
favourable directiont thermal stability of the sub-structure
must be increased and the rate at which the resistance of crystals
to elementary acts of plastic deformation decreases with rising
temperature must be reduced.
There are 10 figures and 24 references: 16 Soviet and
8 non-Soviet. The four latest English-language references
quoted are: Ref. 12 - W.G. Jonston, J.J. Gilman - "Journ.
Appl. Phys.", v-70, No. 2, 1959; Ref. 19 - A. Cottrell -
Trans. of the Metallurg. Soc AIME, V. 212, 1958;
Ref. 20 - D.F. Stein, J.R. Low - Jourim. Appl, Phys., Vol-31.
,No. 2, 196o; Ref. 24 - W.C. Jouston, J.J. Climan Journ.
Appl. Physics, V-31, No. 4, 196o.
ASSOCIATION: TsNIIChM
Card 3/3
a
1-M,

KURDYUMOV, G.V.; LOBODNI", V.A.,, HA11DROS, L.G.
Form of martensite crystals and the orientation of the interpha3e
boundaries in the alloy Cu-Al-Ni. Kristallografiia 6 no.2:210-217
mr-.#.p 161. (MIRA 14:9)
1. Institut metallofiziki AN U333.
(Martensite crystals) (Phase rule and equilibriun)
(Copper-aluminum-nickel alloys)

2021E
I 2i,/61/011/002/014/025
E193/'E483
AUTHORS Arbitz ova , 1,A, , 1~'Iuy dyumov, Gi.V, and Khandro6, L.G.
TITLE . Grourth of Elaqtts Crystals of the Martensitic y~-Phase
Under the Action of Applied Stress
PERIODICAL,, Fi-zil,a trietallov 1 1961, Vol.11, No.2,
J)p - 272-'-180
TEXT. When a martensiti~- transforwat.ton talies place in an alloy,
considerable 53tresse.--j of t--itltiir sicji~ are 2ict up in the matrix by
the firs t-,,o- f orm warrc-nsitc. gra-in~, In Aorue regi.ons these
internal ii-jay bring about nu~Lle;3ticn 4ind growth of new
martensite in others they may have :xtx oppos3Lte effect.
The object of' tile "I'""st1gat"JIL dezicri-bc-d in the present Paper,
wa~i to 6stablish whother the ftirne -,ffect Lan bi- produced by
externally applied itrc-ss,~a, The ~Ypar2.r&~.nt.% were carried out on
a Cu-base allcy, containing, 14,44 Nrt,% A! iind 4~' '75 wt,% Ni, in
W111-ch the ti-ansformiiion 0 1 -,~y -begiri-'3 tit aPP 30*C.
To facilitate x,ifiual examma(i,:-n of thk: rcltif patterns, t1le
experimental r~ipe(--j.mens (mcasuring, 0. x 2,5 x .12 mm), preliminarily
quenched from 900 C' -Werc tr. 70"-C ond polished at this
temperature, Af ter c-oolir)g to room te-riper-ature., several martensite
Card 1/5

5/126/61./o11/002/014/025
Grov"Lli of' R193/R483
needles appeared ort the spe-L:imen st.1rf,,tLt-, but the bulk of the alloy
remained iint.rnnstczmed. The effeLt Of the application of external
stres.% was ,itudicycl 'with the aj.d of a ill(~c-ially designed apparatus,
SC114~11:atically illkizitrAted -111 lpig'l~ The apparatus consistg of a
vacuum chariber (4) whLch Lri.-orporatc-6 a r;:A (,5), mounted on
bellows and u-.ied to li-~ut or cool the test pxe~~e (7) , and a pair of
grlps (6) for fast,~ning the test pit!cc- tThii temperature of the
rod ia changed with thF, aid of a thermos fl,isk, containing a hot
liquid or liquid ni-trogen.) One of rhe gri-p5 is rigidly
atta-hed to the. bGdy of the va-Luut--, chambcz being joined
I -, iht~ other
to a conriecttng r6d uhich ~ntt-rtw th(: vc%z.iju.:i (liamlicr 'through an
piovided with LA A dial gauge indicator
openinq (8)
for measuritig the str-tin i.--3 rigidly at.!~a~-ht~d to the vacuum chamber,
its plunger pres.5inF, aFatn~qt % ro.,
,,11Lttirt7 5pring, dttached to the
COTITICCtIIIA r0d, 010 LAtte" bOLTt~y )()trk+-(l (t, " "'tig dYnalliolneter (11).
StresB is applie~d by -urni.n,- the hand1r, (9) and its magnitude is
shown on an indicator (12), calibrated in hg/nim2. The vacuum
chamber is closed by a Itd (13), provided wi-th a window (14)
through which the test piece can be observfld through a microscope
(2). or photographed with the aid of a photo-camera (1). In one
Card 2/5

20215
S /126/6 1/011/002/014/025
Growth of Elasti-1; E193/E483
series of experimentn.. a tet3t piece was subjected to tensile or
compressive str6s5es and the resultant move.-iient of the phase
boundaries was studied directly by visual examination of the
pol:Lshed spocii-,%en surfaced In other cxpuriiiienta, the test pieces
were cooled froin above the martensitic triinsforinntion temperature
and the resultant variation of the relative quantities of tile 01
and yl phases was assessed, The reault5 indicated that growth,
or a decrease in size, of a marten.9itic phaso crystal can be caused
either by the vnriation of temperat '-ure or by the application of
external qtress, Although the growti, of' a martensitic crystal can
be induced by both fc-n9118 and comprc-~Aive --3tresse.3, it is only
the favourahly oric-tited graitivi that increost, in size in either case.
When tile duLection of the applied stre.--is is iAxanged, crystals with
~ certa-in orient,:itinn of the tuibLit p1cines disappear and grains with
~ different ortentation ore forrm~d in their placc~ The movement
of the phase boundaries takes place both on the application and on
removal of the Pxterital load, When, however, marTensitic grains
are formed under z~onditjLono such thit only one boundary intersects
a whole aingle crystal no movemcnt ol Oii~ boundary takes place on
removal. of the applied I co (1,, The br2tiov.lciur of cry.-3tals with a
Card 3/5
-K

2 15
5/.!-~6/61/011/002/014/025
Growth of Elasti,~, E193/E483
single boundaiy un(Wr the action of applitil )Itess is similar to
that induced by temperature variation iiid -:.an be compared to the
behaviour of elastic twins, intersocting a A.ingle crystal. There
are 4 f igILTCM ari-I 6 Sovie t ref orcn;.o~.i ..
ASSOCIATION., Institut metallofiziki AN UkrSSR
(Inlititute of Phys1cq t)f MI.-,tals AS UkrSSR)
SUIJMITTED~ June 2. 196()
Card 4/5

Growth of Elastic
Fig. 1
Card 5/3
S/126/61/011/002/014/025
E193/E433

21-366
S/126/61/011/004/016/023
E193/E483
AUTHORSt Kardonskiy, V.M., Kurdyumov, V.G., Kurdyumov,_.G.V.
and Parkas. M.D.
TITLE: The Effect of the Grain Substructure and Crystal
Properties on Strength. I. The Fe-Ni and Fe-Si Alloys
PERIODICAL: Fizika metallov i metallovedeniye, 1961, Vol.11, No.4,
pp.6og-614
TEXTt The object of the investigation described in the present
paper was to study the effect of the thermally induced variation
of the properties of crystals on strength of metals in the hard
condition and on the magnitude of the elastic deformation of micro-
domains (distortions of the second type). The experimental work
was carried out on two Fe-base alloys, one containing 25% Ni
and the other 1.15% Si. (The Ni-bearing alloy was chosen for this
purpose because of its specific characteristic, consisting in that
annealing of this alloy at 4500C brings about a complete removal of
the distortions of the second type without significantly affecting
the size of the regions of coherent scattering.) The Fe-Ni alloy
was hardened by quenching, the Fe-Si alloy by cold rolling to
50% reduction in thickness. In addition to the determination
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21366
S/126/61/011/004/016/023
The Effect of the Grain ... E193/E483
(by X-ray diffraction analysis) of the magnitude of distortions of
the second type, Aa/a, and the size D of the regions of
coherent scatterIng, the yield point (as), U.T.S. (OB) and
Vickers hardness number (HV) of both hardened and partially
annealed alloys were measured, and the temperature-dependence of
these properties was determined for both hardened and fully
annealed specimens. The results of the first series of
experiments, carried out on preliminarily hardened Fe-Ni_rlloy,
are reproduced in Fig.1, where HV, as (kg/mM2), D (10 9. cm)
and 6 &/a (10-3) are plotted against the annealing temperature (001
in addition, the diagram shows the temperature-dependence of HV
and as (curves, marked HV(t) and os(t), respectively). Itwill
be 3een that the temperature dependence of a. and HV is quite
different from the relationship between these properties (measured
at 20*0 and the annealing temperature. Thus, as measured rat
4500C is 25 kg/mm2 lower than as measured at 20*C after annealing
at 4500C, the corresponding difference for HV being 90 units.
On the other hand, the temperature-dependence of as and HV is
almost identical with the relationship between Ada/a and the
annealing temperature. The fact that as of preliminarily
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hardened specimens is practically constant after annealing at
various temperatures indicates that cg, meaaured'under these
conditions, reflects mainly the character of the variation of the
grain substructure during heating; in fact, D of specimens,
annealed at various temperatures, also remains practically constant
(see Fig.1). In the next series of experiments, preliminarily
hardened specimens of the Fs-Ni alloy were annealed at 4300C to
attain almost complete removal of the distortions of the second
type, and then the temperature dependence of a. of these
specimens was determined. This was found to be identical with
that of fully hardened alloy, whereby the view was confirmed that
the resistance of an alloy to deformation is not increased by the
presence of distortions of the second type. Owing to the
comparatively low temperature at which the reverse a-+ y
transformation takes place in the Fe-Ni alloy, it was not possible
to use this material to study the relationship between ba/a and
the temperature dependence of annealed specimens. For this
purpose the Fe-Si alloy was more suitable. The results of
experiments carried out on this material are reproduced in Fig.4
which shows: temperature dependence of HV of cold-rolled alloy
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The Effect of the Grain E193/E483
(curve HV(t), white trianglea)i temperature dependence of HV
of specimens annealed at 7500C (curve HVW, white squares)~
variation of HV of preliminarily hardened specimens after
annealing at various temperatures (curve HV, white trianglea)l
variation of D (dots) and A a/a (white triangles) after
annealing at various temperatures. The -temperature dependence of
HV of the annealed specimens reflected the decrease in the
resistance of the alloy to deformation due to the variation of the
properties of crystals with rising temperature; mince the
specimens were annealed at 7000C, their grain substructure should
remain unchanged during subBequent heating and should not affect
the variation of HV. In the case of the cold-rolled specimens,
whose HV was measured at room temperature after annealing at
various temperatures, the variation of HV reflected only the
changes in the micro- and sub-microscopic structure of the grains,
brought about by heutIng to progressively higher temperatures.
This means that in the temperature dependence ,)f HV of cold-
rolled material, HV at each temperature should be determined by
the changes in both the grain substructure and the crystal
properties that have taken place an a result of heating to this
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temperature. Starting from these considerations, the present
authors constructed a "theoretical" curve, illustrating the
temperature dependence of HV of cold-worked alloy, simply by
adding (for each temperature) the decrease in HV due to the
change in the crystal properties (found from the experimentally
determined temperature dependence of annealed specimens) to that
due to the variation of the grain substructure (found from the
experimentally determined variation of HV of cold-worked
specimens after annealing at various temperatures). The results
plotted in Fig.4 (black triangles) were in good agreement with
the experimental curve (white triangles). The results of the
present investigation confirmed the view that strength
(resistance to deformation) of a hardened material is determined
by two factors: (1) the properties of the crystals (resistance to
the movement of dislocations in the crystal regions, free from
sub-boundaries) and (2) the substructure of the crystals (size o-C
the sub-micro-regions, presence of sub-boundaries, degree of
misorientation of the mosaic blocks). There are 5 figures and
9 Soviet references.
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ASSOCIATION: Institut metallovedeniya i fiziki metallov TsNIIChM
(Institute of Science of Metals and Physics of
Meta.b, TaNIIChM)
SUBMITTEDi August 26, 1960
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ILI I E193/E483
AUTHORS: Kardonskiy, V.M.,.Kurdy py,_G,V~. and Perkas, M.D.
TITLEt The Effect of the Grain Substructure and Crystal
Properties on Strength. II. Iron and Nickel
PERIODICALt Fizika metallov i metallovedeniye, 1961, Vol.11, No.4,
pp.615-6ig
TEXT: The object of the present investigation was to obtain
additional experimental evidence on the relative part played in
increasing the strength of metals by the variation of the crystal
structure and by the changes in other properties of crystals.
Nickel and iron were chosen as the experimental materials because
of the different temperature dependence of their yield points below
200C. In the first series of experiments, Vickers hardness BV
and the width B of the (220) lines of iron were measured after
various thermal and mechanical treatments. After lh annealing
at 750 V and B (measured at 20*0 were 65 kg/mm2 and
11 x 1;C-1 rHadians respectively; on lowering the temperature to
-1800C9 HV increased to 185, but B remained practically
unchanged. The specimen was then deformed plastically
(30% compression) at -1800C, after which HV (measured at this
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temperature) was 220 kg/mm2, and' B increased to 31 x 1o-3 radians,
After heating to 200C, B of thij~ specimen decreased to
22 x io-3 radians and HV to 98 kg/mm2. When the specimen was
cooled again to -180*C, hardness increased back to 220 kg/mm2 but
B remained unchanged. These results indicated that an increase
in hardness (strength) can be caused either by the variation of the
crystal properties alone (the increase in HV after cooling to
-1800C was not accompanied by any change of B ) or by the
change of the grain substructure (the increase in HV due to
plastic deformation was accompanied by an increase in B). In
this connection, the authors point out that when an annealed Fe
specimen was compressed at 20*C to 30% deformation, its HV
increased from 63 to 85 kg/mm2 and B from 11 x 1o-3 to
19 x io-3 radians; after cooling to"-1800C, HV increased to
200 kg/mm2. The relatively highereincrease in HV after plastic
deformation at -180*C (see above),was attributed to a higher degree
of dispersion of the grain subatrd'c'ture, formed at -this
temperature. A series of similar experiments was conducted on
ntrast --to- iron,,- -HV__or__&nn*&1Od
-0 gad by- --A -R- r
- olet&--to- -06-increet on lir V --15 -k9_/=2j---n1aAt1C
c
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substructure pla-~ing a relatively small part. In the case of Ni,
J
the part played by the variation of the crystal properties is
small in comparison with that played by the formation of
submicroscopically heterogeneous structure. In both cases,
however, the effect of these two factors is additive. There are
5 figures and 7 references: 5 Soviet and 2 non-Soviet.
ASSOCIATION: Institut metallovedeniya i fiziki metallov TsNIIChM
(Institute of Science of Metals and Physics of
MetaA TaNIIChM)
SUBMITTEDt August 26, 1960
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Elll/E435
AUTHORS: Kurdyumov _V., Nesterenko, Ye.G.
TITLE: Micro-stresses and coherent-scattering regions in
martensite crystals
PERIODICAL: Fizika metallov I metallovedeniye, v.12, no,6, 1961,
883-89o
TEXT: Micro-stresses as well as the small size of regions of
coherent scattering play a part in the broadening and blurring of
X-ray interference lines from martensite In hardened steel. if
martensite crystals are isolated (by electrolytic solution) the
micro-stresses produced by elastic deformation disappear. The
object of the present work was to obtain more precise knowledge
of the nature and causes of micro-stresses arising on quenching
steel. Types Y-12 (U-12) and Y-10A (U-10A) steels were used,
From the broadening and decrease in intensity of the interference
lines of martensite, the crystal-lattice disturbances and the size
of the coherent X-ray scattering regions were determined by mearis
of previously described techniques, The following specimens were
studied: martensite isolated from hardened pieces of U-IOA and
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U-12A steels; hardened filings of U-12A steel; hardened
1.2 mm diameter specimens of U-12A steel,, hardened 4 x 10 x 10 mm
specimens of U-12A steel. Before the X-ray pattern was obtained
a 0.2 mm thick layer was etched off all the specimens except
filings (from which very little was etched off): this was found to
giva carbon contents in the saturated solid solution (martensite)
equal to those analysed in the steel. The results showed that the
value of type II disturbances (ba/a) in martensite crystals of
hardened steel depends on the dimensions of the specimen hardenedi
it is a basic factor that there is no difference between the values
for the very fine filings and those for the 1,2 mm diameter
cylinder. This indicates that the di-sturbances are due to
deformation produced by the formation of the martensite crystals
and deformation produced by thermal stresses, The hardne35
measurements of the hardened cylinders and pieces of U-12A steel
was found to be almost the same; since their type II disturbance
values are different, this means that the high bardness of
martensite in hardened steel is not due to the presence of type II
disturbances, The authors stress that for martensite isolated
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Micro-stresses and coherent- EIII/E435
from U-12A the line broadening 6is due only to the sn"ll block size;
this was found to be 2.6 x 10- cm for U-10 steel and this is in
good agreement with published results (Ref,3: Arbuzov M,P.,
Lysak L.I., Nesterenko Ye.G. DAN SSSR, v.90, 1953, 3). The size
of the coherent scattering region was found to be independent of
the method used to determine them. The uniform deformation
region in martensite crystals is considerably larger than in
plastically deformed metals, confirming the conclusion jointly
published by one of the authors (Nesterenko) and others (Ref.3)
that martensite crystals in a piece of hardened steel are
elastically deformed by forces external to them. For isolated
martensite the situation is entirely different. Static
disturbances can produce changes in the intensity of X-ray
interference without appreciable width change, but special
experiments are needed to check whether this effect could be
responsible for the observed relationships, Study of the effect
of linear dimensions of specimens on static disturbances showed
that for martensite in hardened steel they are due wholly to the
presence of interstitial carbon atoms in the alpha-,iron lattice.
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There are 8 figures, 5 tables and 11 references: 8 Soviet-bloc and
3 non-Soviet-bloc. The three references to English lang"age
publications read as followst Ref.11. Stokes A,R., Proc. Phys. Soc.
v.61, 1948, 382j Ref.5: Warren B.E., Averbach B.L. J, Appl, Phys.,
v.23, 1952, 497; v.21, 1950, 5951 Ref.8. McKechan. M...
Warren B.E. J. Appl. Phys., v.24, 1953, 52,
ASSOCIATION: Institut metallofiziki AN UkrSSR
(Institute of Physics of Metals AS UkrSSR)
SUBMITTEDz May 22, 1961
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TUMANOV, A.T., zaslu?.henr~yy deyatell nauki i tekhniki RSF'SH;
DAVIDENKCV, V.V., akademik; SERENSEN, S.V., akademik;
KURDYUMOV G.V., akademik; BCCHVAR, akademik;
ZAYMOVSKIY, A.S.; SHCHiJ'CV, N.P., prof.;
KUDRYAVTSEV, IN., prof.; VITMa, F.F., prof.; XISHKINA,
S.I., prof.
Ikkov Borisovich Fridman; Dn the fiftieth anniversary,-,f his
birth. Zav.lab. 27 no-7:919-920 161. (MIRA 14:7)
1. Akademlya nauk USSR (for Davidenl-v. Seremzpn). 2. Chleny-
kormspondenty Akademii nauk SSSR (for Kishkin, Zaymovskiy).
(Fridman. Ik