SCIENTIFIC ABSTRACT TREFILOV, I. - TREFILOV, V.I.

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• Collection: Scientific Abstracts
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• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: March 20, 2001
• Sequence Number: 2
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

TREFILOV _.I., yurist
Social insurance payments during temporary transfer to other
work. Okhr. truda i sots. strakh. 4 no.9:3L'r-37 S 161.
(MIRA 14-10)
(Insurance, Social)

-1 -- , "-I
- . TI IRCHFILOV, r'-L'g.ul
Pennionnoye auespechum,ye v SLiSfi; v voprosakh 1 OLVeLDkh (Provldlnrf F,ensions
in tile U~",3a3 cy) P. P. rorokI.c.*,,sIu.y 1 f . F. T)O~,F] f I loslkva', i osI,.ov3kIy
15?57.
1'(*f p. faub:--s.

TMWIL91(,_Xy NISOTA, I.S., red.; SHAURINA, N.D.,
.an--gitrof qnoTich.; BE
takhn.red.
[Calculation of aid for temporary disability] Ischislanie
posobii po vremennoi notrudooposobnosti. Izd,2., ispr. i dop.
Moskva, Izd-vo WeSM. Profizdat, 1959. 103 p. (KMA 13:4)
EVALUATION)
(DIMILITT

BATYGIN, Konstantin Stepanovich; LIRTSMAN, Mikhail Isaakovich;
.TUFILOYY- . trofann ; DENISOVA, I.S., red.;
MARKOCH, K.Ye.,, tekhn. red.
(State insurance allowances; commentary on the legislation
in effect)Posobiia po gosudarstvennom'u stmkhovaniiu; kom-
mentarii k deistvuiushchemu zakonodatelletvu. 2. dop. izd.
Moskva, Profizdat, 1962. 320 p, (MI4 16:3)
(insurance)

TREYIIbV, Ivan Pavlovich
(How to id6reet students of the secondary schools in mathematics]
Irsk zainteresovat' matematikoi uchashchikhoia serdnei shkoly.
Moskva, Gos. uchebrio-pedegog. izd-vo, 1957. 44 P. (MIRA 11:4)
(Mathematics--Study and teaching)

TREFILOV, L.N.
Investigating the freeing of bast fibers. Izv. vys. ucheb. zav.;
tekh, tekst. prom. no-5:54-58 159 (MIRA 13:3)
1. Kastromakoy tekstillnyy institut.
(Bast)
- .07

N
Investigating the process of freeing the fibers from retted ambarY
hemp strav. I.zv.vya.ucheb.sav.; takh.takst.prom. no-3:35-37 160.
(MIRA 13:7)
1-6 lostromskoy tekstillivy institute
(letting) (Amba*j hen)

TRDMDV, M.
Superelevation of the outer rail at curves. p. 478.
RMSTA GIIWR FERAM (Calle Ferate Romine) Bucuresti, Rumania.
Vol. 7, no. 9, Sept. Y-959.
Monthly list of Fast European Accessions (EFAI) LC Vol. 9, no. 2, Feb. 1960
Uncl,

MACUS" St.9 ing.; TREFILOV, Ma, ing.
Rev cailor
Soil stabilization by means of lime and cement.
for 11 no.9016-521 S 163-
w
I

TREFIWV., Me
muddy ties. P. 581-
REVISrA CAIIDR FF2ATF,. (Caile Ferate Romine) Bucurestip k3mania-
Vol, 6s no, 11) Nov. 1958.
Monthly List of East Europe= Accessions (EFAI) IC, Vol. 8, no. 7.,Jdly 1959
Uncle

BARABANSHCHIKOV, A.V.) podpolkovnik, kand. pedag. nauk; GALKIN,
M.I., polkovnik, kand. fil. nauk; D'YACHL14KO., M.I., podpol-
kovnik, kand.ped.nauk,dots.; KOTOV, N.F., polkovnik,kand.
ped.nauk,- KORDBEOIKOV, M.P., polkovnik, kand.ped.nauk;
KHAVCHUN, N.S.) kapitan 2 ranga, kand.ped.nauk,, doto.;
LUTSKOV, V.N., kand. ped. nauk, podpolkovnik; FEDENKO, N.F.,
kapitan, kand. pad. naukj dots.; SHELYAG, V,V., kapit-an I ranga,
kand. fil.nauk; VOST-OKOV, Ye.I., general-mayor, kand. ist. nauk;
KUBASOV) A.F., general-leytenant zapasa, red.; BELCUOV, G.G.,
general-mayor, red., TREFILOV, N.F., kapitan 2 ranga, red.;
MURASHOVA, L.A.,
(Fundamentals of military pedagogy and psychology; L training
aid] Osnovy voennoi pedagogiki i psikhologii; uchebnoe posobie.
[By] A.V.Barabanshchikov i dr. Moskva, Voenizdat, 1964. 383 p.
(MIRA 17:2)

MYLINIK, Aleksandr Iosifovich;.TREFILOV, N.F., red.
(Morals and the discipline of the soldier] Nravstven-
nost? i distsiplina voina. Moskva, Voenizdat, 1964. 95 p.
(MIRA 17:12)

ASTASHOKOV., P.T.., in2b.-polkovnik; TREFILOVp N.F.,, kapitan 2 ranga,
red.; CWAMA, R.I.v tekbF. bred., -
(Military engineer is an energetic teacher]Voennyi i-n-hener -
aktivnyi vospitatell; sbornik statei i ocberkov. Moskva., Voen-
izdat., 1962. 126 p. (Military engineers) (MIRA 15:10)

TSAREV, F.I., polkovnik; TREFIIDV.. N.F.j, kapitan 2 ranga, red.;
CHAPAYEVA , R.I. 9 -i-elEh-n-.--r-e-d-.- '
(Combat honor is dear to us; training the youth of the army and
the navy in combat traditions] Boevaia chest' nam, doroga; vospi-
tanie armeiskoi i flotskoi molodezhi na boevykh tradit.9iiakh. 14o-
skva, Voenizdat 1962. 114 p. (MIRA 15:7)
Nilitary education)

TOBMDANOVSFIYO A.N.J_P_~E-ILO.YL - !;-
Method for intensive short-term tree tapping, Gidroliz, i lesokhim,
prom. 17 no,6:13-14 164. (MIRA 17t12)
1. TSentrallnyy nauchno-iaeleddvatellakly I proyektnyy inatitut
lesokhimichesRoy promyshlonnosti.

TH-MIOV. P.S.
Use of chemicals in tree tapping and their effect on the
vital activity and growth of woods. Gidroliz.i lesokbim.
prom. 13 no.4:20-21 160. (KM 13:7)
1. TSentralinaya zonallnaya opytnaya stantsiya podsochki
TSentrallnogo nauchno-isaledovateliskogo lesokhimicheskogo
instituta.
(Tree tapping)

LUKOV, Grigoriy Demlyanovich, kand. pedagog. naukj dotsent.-polkovnik
TREFILOV N.F. kapitan 2 ranga, red.; JKUZ'M.UI, I.F.p
zapasa 0
tekhn. re.
(Training the will of Soviet soldiers] Vospitanie voli u sovet-
skikh voinov. Moskvap Voen.izd-vo M-va obor. SSSR 1961. 94 P.
IMIRA 15:2)
(Will) (Morale) (Military education)

KORSHUN2 A., lachitelf-pensioner (Gortkovskaya obl.);-TRMLOV, So ;
MOSKALEV, I.; STRMKCYV, L.; MAZUROV, Po
Reader's letters. Pozh.delo 9 no.10:32 0 163. (MIRA 16:12)
. I-Nachallnik inspektsii Gosudarstvennogo pozharnogo nadzora2
Glazovskiy rayon, Udmurtskaya ASSR.

KUZIMINOV, I.I., red.; KISPACH, N.Ya., red.; SLASTENENKO, V.A.,
I red.; TREFILOV, V.A., red.; VORONINA, N.3 red.
(socialist production collective] Sotsialisticheskii proiz-
vodstvennyi kollektiv. Moskva, Mysl', 1964. 230 P.
(MIRA 18:3)
1.,-Moscow. Akademiya obshchestvennykh nauk. '

USSRkhys 10 s
Card
Authors GrIdnev, V. IT., and Trefilov, V. I.
Title. Thereversibility of Martensite conversions during heating
of ferro-carbon alloys
Peziodical Do,kl.,AN S!)SR, 96, Ed. 4, 741 743, June 10-54
Abst ract Describes experiments throuah which the existence of Marten-
Q
site reversIble conversions for tho iron-carbon system was
shown. Seven references. Graphs.
Institution
Preaented. by, Academician n. V. Kurdyumav, March 3, 1054

TREFILOV, V. I.
TREFILOV, V. I.: "Investigation of phase transformationsin the thermal working of
alloys, using increased rates of heating and cooling". Kiev, 1955. Min
Higher Mucation USSR. Kiev Order of Lenin Polytechnic Inst. (Dissertations
for the Degree of Candidate of Technical Sciences.)
Sot KnizhnMa letopial No. 49, 3 December 1955. Moscow.

137-58-6-13270
Translation from: Referativnyy zhurnal, Metallurgiya, 1958, PIr 6, p 300 (USSR)
AUTHORS: Gridnev, V.N., Trefilov, V.I.
TITLE: On the Thermodynamics of Martensite Transformations (K
termodinamike martensitnykh prevrashcheniy)
PERIODICAL: Sb. nauchn. rabot In-ta metallofiz. AN UkrSSR, 1957, Nr 8,
pp Z9-41
ABSTRACT: The mechanism of self -retardation of martensite transform-
ation is discussed. Assuming that retardation is caused by
omnilateral compression of retained austenite [Shteynberg, S.S.,
Izbrannyye stat'i (Selected Articles). Mashgiz, Moscow, 1950
it is stated that the retardation is caused by a decrease in the
difference between the thermodynamb~ potentials of the austen-
ite by the forming of a martensite framework. An equation con-
necting the degree of transformation M and the overcooling rel-
ative to the martensite point TH, is obtained in the form
Mz = K(TH - T). The fact of increasing compression of the
retained itu'stenite during a decrease in temperature (to -1800C)
is confirmed by measuring the austenitc-lattice spacing in
Card 1/2 tempered steel containing 0. 841o C, 16. ljo Ni, and 1. 6jo Mn;

137-58-6-13270
On the Thermodynamics of Marten5ire Transformations
after various degrees of cooling below the TH point, the spacing of the
austenite lattice is qv, 3.595 angstrorn;. upon cooling to - 500 and formation
of 501o martensite it is 3.590 angstrom, and after cooling to -180 it is
~~3.585 angstrom.
D.B.
1. Martensite--Thermodynamic properties 2. Steel--Transformations
3/ Aus%enite--Metallurgical effects
Card 2/2

0 u I
I L
20-1-16/44
AUTHOR3: Grinev, V.11., Trefilov, V.I.
TITLEs On the Relation between the Parameters of the Crystal Lattice of
Austenite with a Temperature at which Martensite Transformation
Begins in Alloys of Iron and Carbon (0 svyazi parametrov kristal-
licheskoy reshetki austenita s temperaturoy nachala martensit-
nogo prevrashcheniya v splavakh zheleza a uglerodom)
PERIODICALt Doklady AN SSSR, 1957, Vol. 116, Nr 1, pp. 60 - 62 (USSR)
ABSTRAM First, several previous works dealing with this subject are men-
tioned. According to thorough investigations oarried out, tfie
lattice parameter of austenite in martensite transformations de-
pends a little upon the carbon content of the steel. According
to the above mentioned previous work, the parameter of-he re-
manent austenite changes on the occasion of martensite trans-
formation from the martensite point to room temperatures only
under the influence of temperature. However, the investigation
of the martensite transformation points in the direction of yet
another factor which has hitherto not been considered: From the
beginning of the transformation onwards needle-shaped martensite
Card 112 plates are formed in the course of continuous c3oling, which

20-1-16/44
On the Relation between the Parameters of the Crystal Lattice of Austenite vith
,,a Temperature at which Martensite Transformation Begins in Alloys of Iron and
Carbon
gradually form a very firm skeleton structure. In the cut out
places and cells of this skeleton the not transformed remanent
austenite remains. Martensite transformation is accompanied by
a positive volume effect. Interesting data in this respect may
be found in the paper by Vefer et al. (ref-4). The parameter of
the austenite changes considerably at the temperature at which
the transfdrnation of martensite begins and with an increase of
the carbon content of the sted. The attempt made by the authors
to determine data concerning the compression of austenite on the
occasion of the transformation of martensite is discussed in
short. The thus found dependence of the parameters of austenite
on the quantity of the martensite formed is illustrated in form
of a table. The direct data obtained in this way confirm, the
compression of the austenite under the effect of martensite
transformation. There are 4 figures, 1 table and 6 references,
4 of which are Slavic.
PRESENTED: April 17, 1957, by G.V.Kurdyumov, Academician
SUBMITTED; December 20, 1956
AVAILABLE: Library of Congress
Card 2/2

GRIDNEV, V.H. [Hridniev, V.N.J; 7WIIA)V, v.j.
Phase chan&es in steel during electric tempering [with summarv
in EngliahJ. Ukr. fiz. zhur. 3 no.6:?96-801 N-D '58.
(14IRA 12:6)
l.Institut metalefiziki AN USSR.
(Steel-Metallography) (Tempering)

18(T) PfLAS3 I BOOK UPWITATZON SOV/3355

AkAdaulya nauk S33R. InGtitut Astallurgil. Nauchnyy.,Govoz po
problems zharoprachnykh aplavov
Isaladovanlys, pa thALroprochnym splavan. t. IV (Studies on Hoat-7 s-
Istant Aaloys, vol. 4), Moscow, lzd-vo AN S53R, 1959. 400 p.
0
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.
es pr
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cop
Irrata. allp trA*rt*d. 2,2

Ed. or Publishing House; V. A. Klimov, Tech. Cd.z A. P. Gu3evs;
Editorial -Board: 1. 11. Bardlo. Academician; 0. V. Kurdruzov,
Ac-A--Iclanj 0. V. Agayov; Con-a pOndLM9 Member. =R Academy f
3ciences; 1. A. Oding, 1. 9. favlov, and 1. P. Zudin. Candidate
of Technical 3clences.
MR?= i This book In intended for metallurgists concerned with
. the structural metallurgy or alloys.
COLRAGEt This is a collection of specialized studies Of VariOUG

I n the structural metallurgy or halt-realetant alloys.

rob amns I
-
some with de
al ,In.i,l.a
ti
g
c
,
oee are concerned with theore
criptIona of new equipment and methods, others with propertl:.
phec=n& occurring under
of specific materials V&rLOU:
d
specified conditions irt studi and reported on. For d*'Allo.
2" Table of Contents. 'the articles are sc,compw~t4d by & num-
Soviet and
stud!es (cont.)
3-/335 5
aaXLTRI-A-?-- And Z- V. Charn*nko. Zffoct of plea tic
-
-
-
-
Deformation at Low
7.
.ia
r
jejii78-on the Hest-r eslatxnt
"roPerties Of TYP* 18-8-TL Austenitic Steel
214
3avitakiy. y.. 11., W ~~Iki . .
~Vlk R a-yetallization or
Metals TI
t

o"
ium, kirnium, Tantalum, Rh.~W,
and Tungst4a. " Their
Alloys
218
orldn'"I V, W-, V- 1- Trsttjov. and &. K. But;rlonko. 3froct
226
Ageyow, X. V and V. A. Trap4Znlicov, ft-oduction of pure
237
--
TW-
T0,XAYAtz&AkO, and A. X,_�jjUr-Ia.._A Study of the

Constitution
VI-441- of the Ternary System Chromlu;3-i~rggten-ftlybdn.
2

Card 8/12 5T

e1~
18(4.T); 25(l) PHASE I Boox EXPLOITATION SOV/2306
Akad0alYa nauk Ukrainakoy SSR. Institut mstALlOf`lz1kI
VOPPOsy fiziki metallov I metallovedenlya. (Problems In the Physics
Of Firtals and Notallography) KLyev. lzdo-vo AN OcrainskLy SSR,
1959. (Serleas Ito: Sbornlk n,2uchnykh rUbOt. Nr 9) Errata
allp inserted. 3,000 copies printed.
Zd. or Publishing Houses V.L. Shkuzrico; Tech. Ed.: R.I. Yeriftova;
Sditarlal Board; V.K. Svechnlkov. Academician. Academy or Sclencc~bl\
Ukrainian 33H (Reap. Ed.); S.D. Gortarikess, Doctor of Physical
AW Mathematical Sciences; and I.Ya. Delchtyar, Doctor of
T40hulaal Sciences.
TURPOSas This collection or articles in intended for scientific
workers, aspirants, and engineers In the fields or the physicL
Of metals. notallography, and matallorEy. It may A1&O be useful
to students of advanced courses In metallurgloal and physical
faculftes.
COW=[ This collection of articles deals with the following
topics$ affect of hi"i ~-spes -tWii!iiz-'ficaz' treatment '-dtr6rina~;___'~,-
tines, and crystallization Conditions On phase transiormat Ions.
structures, and properties or metals and alloys; the effect of
additional alloying component& on volumatrIc and Lntercrystallinal~-
diffusion In alloyal and the effect or repeated quench hardening
and radioactive and ultrasonic treatment on the physical proper-
of alloys. No perbonalit as are mentioned. References
OW moveral*dt ths articles.
larikov, L.N., and Problem or the Effect
of Ultrasonics on FFFaaa TrasssrormatiOn3 Of Carbide Metals
and Alloys 50
This artiol* presents A study Of the effect of ultrasonic
treatment on the aging process of duralumin and an allay
composed of lead and 6 percent tin. Data obtained arm
prasentad In diagrams.
GrLdnev. Y.9- Effect or High-speed Heating on the Structure
05ff-FR5ertles of Steel 54
The author describes an experimental Investigation in
which special devices were used for the 31W'1t4uGOU3
recording or time, temperatu.-o, elongation. and charges
or voltage and amperage. Data presented In the article
were obtained at the Laboratory for Heat Treatment,
Klyevakly polltdkhnichaskly in3titut (Kiyov Polytechr-Scal
~__1uxtLtuta1,.aW at the Inctitut metalloriziki, AN 03311t
(Institute for the Physics or Metals, Academy of Science*,
YkrSSR).
arLdnev, V.N. and V.I. TreCtlov. Metastable Trunnforma-
tions in Itutectio Cu-Al Alloys 68
The mechanism and kinetics of P"30 trAn3fOr=%JLtiOn3 are
discussed in thin paper. Simultaneous motion picture
recording with oacillographle ZWIBXU~ing or temperature
=ad* possible the accurate determijuslon of all para-
motors Investigated. The technique uned In the experl-
ment Is described, and transformt-4on3 are presented I=
the form or photographs and diagrams.
Gridnev, V.N., V.I.-Trefilov, and A,2__2mLc_h_ngk_7.
Change in Mechanical P~OpertlaB or TI-Pe A11073 Due to
Heat Treatment 82
Low-allOY Tl-?* samples (2.5hon. diaoseter. 22mm. long),
sintered, forged, and machined, were used. Results
___fflLrq_#hWM. Iq_d~agramz._

l
"t
V.N. Oridnev, and Y_I__xMrJlZ,_ Changes
L
"R

In :ZctM;W nd Properties or Powder us
i
t
t
Vanuum Rolling 89
Samples of titanium IW-1, made at the T3ontral-hyy
nauchno-isaledovatel-skiy Institut chernoy metAllurgil
(Central Scientific Research Institute or PerrQU3 Meta-
llurgy) " rolled In the laboratory vacuum mLlI them,
were subjected to micro- and X-ray structural arA17319
ond mechanical testing at room temperature. Results A"
dIscussed and conclusions drawn.
Orldnev, V.N., and V.T. Cherepin. Phase Transformation&
in Caxbon-free Iron-AI1_o_y-s-VaFrng Electric Heating 98
This article presents a study or change,& from alpha to
Iron. dilatation, the critical point, and the
"
NL Point for vu-Ious Iron base alloys (Fe-Cu. ft-W,
Fq_TI' 70-Ni. ft-Cr, and ft-31) in the annealed to well
as the ?uenohod state at varying rates of temperature
Change 5W to 4000*0 per second).
Card 7/12

SOV/180-59-2-11/34
AUTHORS: Gridnev, V.N. and Trefilov V I __~[Kiyev)
TITLE: Structural Changes During Electrical Tempering of Steel
(Strukturnyye izmeneniya pri elektrootpuske stali)
PEPIODICAL: Izvestiya Akademii Nauk SSSR7 Otdeleniye tekhnicheskik'a
nauk, Metallurgiya i toplivo7 1959, Nr 2, pp 62-69 WSSR)
ABSTRACT: The work described, in some of which D.V. Lotsko and
N.F. Chernenko participated, was carried out with types
U8A and U12A carbon steel. Specimens 1.2 to 1.6 Mm in
diameter were subjected to hardening from temperatures
ensuring solution of secondary cementite in water
followed by supercooling in liquid air to reduce the
residual-austenite content. The specimens were then
subjected to electric tempering by the contact method
with heating rates varying from hundreds to several
thousand degrees per second. As soon as the required
temperature had been reached the current was switched of.'L*
and the specimens were quenched with water with cooling
rates of 2500 to 3000 OC/sec. During heating oscillo-
graphic recordings were made of -the heating and dilato-
Card 1/)+ metric curves. For comparison some of the supercooled
specimens were subjected to ordinary tempering for an

sov/18o-59-2-11/34
Structural Changes During Electrical Tempering of Steel
hour at various temperatures. Changes in block structure
and second-type internal distortions were studied with
the aid of X-ray structural analysis, calculations being
made from the line-thicknesses according to methods
developed by G.V. Kurdyamov and L.I. I;ysak (Refs 1-3).
The choice of lines depended on tempering temperature.
The changes in second-order distortions depending on the
temperature for various speeds of tempering are shown in
Figs 1 and 2 for U12A-and U8A steels, respectively. The
effect of the electric -compared with ordinary tempering
was to delay the distortion-relation processes and the
growth of alpha-phase blocks. Rapid cooling for the
prevailing experimental conditions had practically no
effect on results. With low and medium tempering
temperatures some differences between the two steels
appeared. Figs 3, 4 and 5 shcw the block dimension as
functions of temperature and electric-tempering tempera-
ture for U12Aand U8A steels, respectively Comparison
of electric tempered with an 80% deformed Zby drawing)
Card 2/4 specimen showed that for U12A steel the same changes in
distortion and block size could be obtained by electric

SOV/180-59-2-11/34
Structural Changes During Electrical Tempering of Steel
tempering at 580 - 620 OC, at 1000 - 10000 OC/second.
Static distortion of the third-type was also studied to
provide further comparative information. It has been
sho,im that this type accounts for about all deformation-
produced increase in energy of metal. The authors
measured these distortions by methods described in the
literature with X-ray photography at room temperature
and neglecting changes in dynamic distortion. The
tabulated results of some measurements show that the
magnitude of static third-type distortion in steel sub-
jected to electric tempering to temperatures up to
approximately 6500C is very similar to that in work-
hardened metal. Discussing the influence of electric
tempering on hardness phenomena the authors mention their
conclusive experimental proof that only a ferrite-carbide
mixture is present in specimens quenched from tempera-
tures over 6000C. They have also found that in such
specimens the third-type distortions are of similar
magnitude to those produced by strong plastic deformation.
Card 3/4 The authors discuss the relation between block size and
third-type distortions. They deduce an equation for th_-

SOV/180-59-2-11/34
Structural Changes During Electrical Tempering of Steel
relative elongation to fracture in terms of a coefficient
characterizing the material, a lattice parameter, grain
diameter, Poisson's ratio and a coefficient representing
the form of dislocation fixing. Fig 6 shows the
relations graphically while Fig 7 gives test results
which confirmed the relations deduced. These and the
results of hardness determinations for U12A and U8A
steels (shown in Pigs 8 and 9 respectively as functions
of electric-tempering temperatures) confirm the-superior
properties produced by electric tempering. The authors
suggest that further investigations are necessary)
especially on its possible use instead of alloying.
Card 4/4 There are 9 figures, 1 table and 17 references, 13 of
which are Soviet and 4 English.
SUBMITTED: January 91 1958

GROMT., V.H. [Hridniev, V.N.1; WHAKOV, V.N.; TREFILOV. V.1.;
.AL Resistance of metals to deformation during phase transforsation.
Ukr.fiz.zhur. 4 no.4:526-527 Jl-Ag '59. (MIM 13:4)
1. Institut metallofiziki AN USSR.
(Deformations (Mechanics)) (metals)

BUTYJMO, O.K.; KUhDYUMOVA, I.G. [KurdiUmOva, I-H-); TREFILOV,V,~.
Determining the activation energy of chromium recrystallization,
Ukr.fiz.zhur. 4 no.6:813-814 N-D t59- OaFA 14:10)
1
1. Institut metallofiziki AN USSR.
(Chromium crystals)

GRIDNE7, V.11.; RAFALOVSKIY, V.A-r, TRUILOV, V.I.; CHMMIKO, N.F.
I---
Phase and structural changes in heating Ti-Gr alloys. Sbor. nailch
rab. Inst. metallofiz. AN URR no.lOt77-85 159- (KM 13:9~
(Titanium-chromium alloys-Metallogra hy)
(Metals, Effect of temperature 0n3

GRIDITEV. V.11.;, TREFILOV, V.I.
Carbide phase in carbon steels during electric tempering. Sbor. nauch.
rab. Inst. metallofiz. AN UM no.10:86-93 159. (MIRA 13:9)
(Steel--Heat treatment) (Phase rule and equilibrium)

GRIDNW, V.N.; PBTROV, Yu.N.; TRAFILOV, V.I.
Xlectron microscopy of the carbiie phase produced by tempering and
electric tempering of carbon steels. Sbor. nauch. rab. Inst. metal-
logiz. All URSR no.10:94-103 '59. (MIRA 13:9)
(Y,Lectron microscopy) (Steel--Heat treatment)
(Phase rule and equilibrium)

GRIIM.
Microstracture of martensite in tatanium-chromium alloye. Titan
i ego splavy no-3:58-60 160. (MM 13:7)
(Titanbam-Chromium alloys) (Martensite)

GRIDW. T.N. I -Twrrov, va. I cHmmm, N.Y.
Transformations durIng the electric beating of co=ercial tita-
nium in titanium-iron alloys, Titan I ago sPlavY no.3t6l-65 160.
(Titanium-iron alloys-Heat treatment) (Titanium--getallography)

32030
ILIVII JL118, ~JCJ)b S/601/60/000/011/006/014
fgl~LK' D207/D304
AUTHORS: Gridnev, V. N. Petrov, Yu. N., Rafalovskly, V. A.
and Trefilov, V. I.
TITLE: Investigating the w -phase formation in
titanium alloys
SOURCE: Akademiya nauk Ukrayins1koyi RSR. Instytut
metalofyzyky. Sbornik nauchnykh rabot. no. 11.
1960. Voprosy fiziki metallov i metallovedeniya,
82-86
TEXT: The authors investigated, by electron microscopy and
electron diffraction, formation of the w -phase in Ti-Cr and V~
Ti-Fe alloys. The alloys were prepared in an are furnace filled
with argon and were then forged and annealed. The co-phase was
produced by quenching in the alloys with 5 or 8% Or and with
5% Fe; the co-phase particles were highly dispersed at random,
and they could be easily separated from the matrix in the Ti-5% Pe
Card 1/3

32030
S/601/60/000/017/006/014
Investigating the... D207/D304
alloy. In the alloys with 12% CR or 8% Fe, quenching produced
the0 P-phase in supercooled state; isothermal-treatment at 200 -
350 C decomposed this P-phase into the 40-phase and a Cr-rich
13-phase. Such isothermal treatment increased the sample length
and its hardness. The w -phase particles grew in size during
the isothermal treatment, and the rate of growth indicated a
noncoagulation process.0 The dimensions of the W-particles did
not exceed 1200 - 1600 A; beyond this size, the co-P +-_ trans- V\/
formation took place. The w-particles produced by the isother-
mal treatment were concentrated along the grain boundaries of the
0 -phase. Further experiments showed that the cu-phase was
formed also by 20 - 25% plastic def8rmation of the 12% Or or
5% Fe alloys, but cooling to _196 0 did not produce the -r-
phase in the 12% Or or 8% Fe samples. These experimental ob-
servations were accounted for by a theor of the w -phase forma-
tion which unifies the suggestions of (1~ martensite-type diffu-
sionless transformation and (2) decomposition of a metastable

32030
B/60 60/000/011/006/014
Investigating the... D207X304
solid solution with the w-phase as an intermediate stage. There
are 5 figures and 9 references: 3 Soviet-bloc and 6 non-Soviet-
bloc. The reference to the English-language publication reads
as follows: F. Brotzen, E. Harmon, A. Troiano, J. of Metals,
5, no, 2, 2, 231, 1953.
Gard 3/3

8/601/60/000/011/013/014
D207/D304
AUTHORS: Minakov, V. N., Rudoy, A, Po, and Trefilov,
V. 1.
TITLE: A dilatometer with a capacitance detector
SOURCE: Akademiya nauk Ukrayinslkoyi RSR. Instytut
metalofyzyky. Sbornik nauchnykh rabot. no.
11. 1960. Voprosy fiziki metallov i metallo-
vedeniya, 158-159
TEXT: The authors describe a simple dilatometer with rapid
response suitable for studies of phase transformations at high
rates of heating. The detector is a capacitor with a movable
(b) and fixed (a and c) electrodes (Fig. 1). The change of
length of a sample is transformed into a change of capacitance
by motion of the movable electrode. The two electrode systems
(ab, cb) form parts of two separate oscillatory circuits working
at or near resonance. The resonance is distributed when the
Card 11~3

S/601/60/000/011/0171/014
A dilatometer with... D207/D304
capacitances ab and bc are altered. This affects the natural.
frequencies of the circuits and the anode currents of a double
triode GHi5n (6N15P). An induction coil L 2 and capacitances
C1 and 0 2 form the grid circuit, while inductance L 1 and the
the capacitance 0 ob form the anode circuit of the left-hand
part of the double triode. Both these circuits are loosely
coupled, and the coils L 1 and L 2 are placed on the same axis.
The grid circuit is tuned by means of C 2 so that any change of
Ccb produces a directly proportional increase of the anode cur-
rent, The oscillator on the right-hand side contains 0 ab and
is constructed in a similar fashion. The circuits are assembled
from intermediate frequency filters of the audio parts of the
?'Rekord" television set,, When the capacitances Cab and C cb
are varied, the current in one triode increases and falls in the
Card 21~3

A dilatometer with...
S/601/60/000/011/013/014
D207/D304
other. The difference current is passed through loop no- 8 of
an oscillograph m no-a (MPO-2) connected between the triode
a.nodes. The direct proportionality between the oscillator indica-
tion and the dilatometer displacement is obtained by suitable se-
lection of the ga~ between the fixed electrodes a and c and
of the working regions oa the resonance curves of the oscillators.
The instrument constructed by the authors has a linear charac-
teristic for capacitor plate displacements of 0 - 1 mm, The in-
strument gives reliable dilatometric curves when used in conjunc-
tion with a loop osaillograph. The oscillograph readings are
practically unaffected by the cathode drift and supply voltage
variations. There are 2 figures and 2 Soviet-bloc references.
Z-Abstracter's note: Essentially complete tranalation,l
SUBMITTED: September 150 1959
Card 3/

84469
S10201601134100610121031
B019/BO67
AUTHORSs Gridnev, V. N., Trefilov, V. I., and Minakov, V. N~
TITLEi Martensitic Transformation in the System Titanium
Zirbonium
PERIODICALs Doklady Akademii nauk SSSR, 1960, Vol. 134, No. 6,
pp. 1334 - 1336
TEXTs The authors studied the temperature dependence of the martensitic
transformation on the composition of the Ti-Zr alloy. Furthermore, they
examined the existence of a reverse martensitic transformation. Iodides
of both metals were used for the production of the alloys. The
production method is described in detail. The apparatus used for the
investigation of the phase transformation was described in Ref. 3. It
allowed the simultaneous determination of temperature, dilatation curves,
voltage drop in the sample, and the amperage of the current heating the
sample. Heating to 950 - 1000 0C was effected in qu4rtz ampoules,
quenching was carried out at a rate of 1000 - 1500 0C/sec by previously
crushing the ampoules in the water. The X-ray diffraction pattern showed
Card 1/3

M169
Martensitic Transformation in the System S/020/60/134/006/012/031
Titanium - Zirconium B019/BO67
only a martensitic alpha prime phase; an undercooled beta phase could not
be found. The authors arrive at the conclusion that the residual beta
phase in the Ti-Zr alloy is the smaller the lower the amount of nitrogen
and oxygen impurities in the alloy.. The alpha prime phase has the
characteristic martensitic structure, and the reverse marten8itic trans-
formation could be proved on heating (5000C/sec). Fig. 2 graphically
shows the transformation temperatures for direct and reverse martensitic
transformations as a function of the composition of the alloy. In the
range from 40 to 80 at%, the transformation temperature is independent
of the composition. The authors conclude from the results that in the
ranges from 0 to 40% Zr and from 80 to 100% Zr the transformation A-)-a'
takes place on quenching in water or in an argon jets With accelerated
heating the transformation al-i-A occurs. In the range from 40 to 80% Zr,
the same transformations occur on quenching in water and on rapid
heating. On cooling in the argon jet (200 - 300OC/see), however, P-cj
transformation occurs besides the transformation mefitioned, Great
significance is ascribed to the formation of the6j-phase in the Ti-Zr
system, and it is discussed J.n detail. The results of other authors are
described, and it is found that the difficulty in producing the &j-phase
Card 2/3

Martensitic Transformation in the System 6/020/60/134/006/012/031
Titanium - Zirconium B019/BO67
in the system investigated lies in the fact that the temperature of the
V)&j' transformation is below the temperature of direct P--). a' trans-
formation. The&)-phase is formed on undercooling a certain amount of the
P-phase to the temperature of formation of the &)-phase. Yu.A.Bagaryatskiy
(Refs. 5 and 6) is mentioned. There are 3 figures and 8 references:
3 Soviet, 3 US, I German, and I British.
ASSOCIATION: Institut metallofiziki Akademii nauk USSR (Institute of
Metal Physics of the Academy of Sciences Uk
FRESENTEDs May 25, 1960, by G. V. Kurdyumov, Academician
SUBMITTEDs March 22, 1960
Card 3/3

ss 0'0
1%'1185
27032
S/125/61/000/()04/001/013
A1611A127
AUTHORIs Grabin, V. F., Ourevich, S. M., Rafalovskiy, V. A., Trefilov, V. I.
TITLE: Investigation of aging processes in welds on biphase titanium alloys.
Instalment I - Aging of welds in the post-welding state
PERIODICAL: Avtomaticheskaya svarka, no. 4, 1961, 3 - 12
TEM. The purpose of the described investigation was to compare aging pro-
cesses in biphase titanium alloys with different additions of 8-stabilizers. Welds
were studied in the as-welded state, and after heat treatment. The three experi-
ment alloys were the commerciaj. BT6 (VT6) with 6.1% Al and 4.1% V, and two test
alloys designated no. 1 and containing 2.5% Al, 9.7% V and 3.8% Mn, and no. 2 -
with 6.34% Mn. The investigation methods were the following: metallographic,
electron-microscopic, X-ray, dilatometric, measurement of electric resistance and
hardness, and tests for mechanical properties. Collodium, carbon and silver-carbon
prints were used for examination with the Y3M-100 (UEM-100) electron microscope.
The phase composition was determined roentgenographically with copper radiation
and nickel filters. The differential vacuum diletometer had been described former-
ly [Ref. 1l: V. F. Grabin, V. G. Vasillyev, V. A. Rafalovskiy, "Avtom. avarka",
Card 1/4

27032
S./125/61/000/004/001/01'3
investigation of aging processes in welds on... A161/A127
no. 3, 1960]. The electric resistance was measured in a high-temperature vacuum
unit. Heating for heat treatment and artificial aging was produced in evacuated
quartz ampoules. Welded specimens were prepared by joining 3 to 6 mm thick sheets
by butt welding with electrodes of the same metal as the base metal, by submerged
arc with An-Ti (AN-M) flux. The article presents the first part of results - ob-
tained with welds that were not heat-treated. Graphs and electron microscope
photo-micrographs are included. The formation of the phase omega was observed in
the no. 2 alloy only M-Mn), directly after the welding. The test results con-
firmed previous conclusions concerning the stability cf welds on VT6 alloy [Ref .14;
S. M. Gurevich, V. F. Grabin, "Av-tom. svarka", no. 4, 1959]. The article includes
references to Soviet-bloc and non-Soviet-bloc publications in connection with data
an embrittlement in titanium alloy welds. Conclusions: 1) The possibility of
W-phase formation in weld metal and the adjacent heat-affected zone in binary
Ti-~Mn alloys (no. 2) has been experimentally proven. The formation of this phase
directly after welding causes embrittlement. 2) The W-phase seen in the electron
microscope has the shape of round or oblong segregations that are distributed non-
uniformly. The segregations were, as a rule, observed inside grains. 3) The w-
phase was not found in welds that contained A-stabilizers (vanadium and manganese
aggregate content as in the no. 1 alloy), and an o~-stabilizer (aluminum). But
Card P_/4

27032
S/125/61/000/004/001/013
Investigation of aging processes in welds on... A161/A127
weld metal alloyed with manganese alone was highly prone to aging accompanied with
the formation of W-phase. 4) Aging was most intensive in the 200 - 4500C tempera-
ture range. Long isothermic soaking (to 100 hours) did not eliminate brittleness,.
which is apparently caused by the ov-phase segregation on grain boundaries as a
result of the 8~ + oj _j, 3 + x transformations - 5) Welds in the VT6 alloy in the
post-weldirZ state are sufficiently stable and do not embrittle in artificial ag-
ing in the 200 - 5000C range. Hence it is wrong to use high-temperature 2 treatment
fcrthe VT6 alloy welds when the required strength is not above 100 kg/mm . Temper-
ing for stress relief will be sufficient. There are 6 figures, 3 tables and 14
references: 4 Soviet-bloc and 10 non-Soviet-bloc. The references to the four most
recent English-language publications read as follows: E. L. Harmon, I. Koozol,
A. R. Troiano, Mechanical Properties Correlated with Transformation Characteristics
of Titanium-Vanadium Alloys, "Trans. Amer. Soc. Metals", v. 50, 1958; A. I. Grie4
I. R. Doing and P. D. Frost, Cor-relation of Transformation Behaviour with Meehan'-
cal Properties of Several Titanium-13ase Alloys, "Tran . Met. Soc. Amer. Inst . Min.",
"Metal Eng.11, 215, 1959; R. W. Douglass, F. C. Holden, H. R. Ogden and R. T. Yaf-
fee, Effect of Microstructure on the Mechanical Properties of Ti-V, Ti-Al-V Alloys,
"Journal of Metals", v. 12, no. 1, 1960, A. 1. Griest, A. P. Joung, A Study of
Beta Embrittlement in High-Strength Titanium Alloys, "Battelle Mem. Institute", 1958,
Card 3/4

27032
s/125/6i/ooq/oo4/ooi/o13
Investigation of aging processes in welds on ... A161/A127
ASSOCIATION: Ordena Trudovogo Krasnogo Znameni Institut elektrosvarki im. Ye. 0.
Patona, AN USSR ("Order of the Red Banner of Labor" Electric Welding
Institute Im. Ye. 0. Paton AS UkrSSR) (V. F. Grabin and S. M. Gure-
vich); Institut metallofiziki AN USSR (Institute of Physics of MetaI6
AS UkrSSR) (V. A. Ratalovskiy and V. 1. Trefilov)
Card 4/4

3/1,37/6 Z/CCO/008/0 338/G6 5
A0061A 10 1
AUTHORS: Gridnev, V. N., Trefilov, V. I., Lotsko, D. V.., Chernenka, N. F.
TITLE: On the mechanism of phase transformations in Ti-Cr alloys
PERIODICAL: Referativnyy zhurnal, Metallurgiya, no.*8, 1962, 36, abstract 81221.
("Sb. nauchn. rabot In-ta, metallofiz. AN.UkricSR", 1961, no. 12,
37 - 45)
TEXT: TI-alloys containing 0.5 - 10.5,111 Cr were melted in an are furnace.
From the.ingots, wire,1.6 - 1.8 mm in'diameter, was manufactured after forging.
During the electric heating of the specimens, temperature and dilatometric
curves, and the dropping of the current'voltage and intensity were recorded. The
alloys were quenched in an argon jet at 200 - 300 degree per second cooling rate.
The quenched alloys, containing up to 5 - 5.5% Cr, have an :A! -phase structurl~. At
a higher Cr-content the temperature 6f martensite transformation decreases ab-
ruptl~. During the heating of quenched alloys reverse transformation takes place
according to martensite kinetics. The temperature of-reverse transformation
depends only on the Cr content and not on the heating rate (150 - 3,000 degree/sec).
Card 1/2

S1 1 __37/6 2100,01008103810665
On the mechanism of phase transformations in... A006IA101
In alloys with 5.5 - 6% Cr, W-phase is formed. The temperature of V-phase forma-
tion is about 3100C and does not depend on the composition or the cooling rate.
The temperature of reverse transformation W - R is by 80 - 100aC higher and also
depends neither on the composition nor the cooling rate. The growing crystals
of the martensite phase cause the formation of martensite crystals in the adja-
cent grain when they encounter the grain boundary; the magnitude*of the crystals
depends upon the dynamic collision force. The domain structure of mar-tensite-
needles is noted. The authors studied also the transformation occurring
during the heating of annealed alloys. It was established that it begins at
850�100C independent of the heating rate and the Cr con-tent. There are 10 ref-
erences.
P. Novik
[Abstracter's note: Complete translation]
Card 2/2

S11251,R)SO100610011010
11 ID D040/D112
AUTHORS.- Grabin, V. F., Gurevich, S. M., Rafalovskiy, V. A.,
Trefilov, V. I.
TITLE: Investigation of ageing processes in biphase titanium alloy
welds. 11 installment. - Ageing of heat treated welds
PERIODICALt Avtomatieheakaya svarkaol~no. 69 194v 3-13
A
TEXTs Results of investigation of the structure and mechanical properties
of titanium alloy welds in the initial state were presented by the authors
in instalment I (Ref- 33 "Avtom.avarkallp no, 4, 1961). The II Instal-
ment presents the results of investigations made after heat treatment con-
sisting in heating specimens to eOO-900001 quenching in water, and subse-
quent ageing at 200-6000C in evacuated quartz ampoules. The studied alloys
were commercial B76 (VT6)(Ti-Al-V system), and two experimental compositions
- No. I (Ti-Al-V-Mn) and No. 2 (Ti-Mn). 1he reason for the investigation is
the ever more extensive application of high-strength biphase, titanium alloys
for welded structures ' and the embrittlement in welds. The chemical composi-
tion and properties of the three studied alloys were given in Ref. 3. The
Card 1/8

S/12 22937
OY611000100610011010
Invootigation of ageing proceones ... D04 D112
ageing process was studied by measurements of hardness, electric resistance
and thermal expansion, and with X-ray and electron microscope observatio.-o
The results are discusbed with references to data of seventeen other works,
Soviet and foreign. The minimum hardness was established in VT6 alloy welds
with the lowest quantity of ! (10%) after quenching; in mixed and
structure it reached 550-600 Hv, Maximum hardness was reached faster at a
higher ageing temperature. In VT6 the maximum hardness depended only little
on the quenching temperature, but in the No. 1 and 2 alloys this dependence
was more pronounced. The formation of- upon isothermic decomposition was
accompanied by volume reduction of specimens and change of the sign of the
temperature caeffici 'ent of electric resistance. After sufficiently long
holding perio 'ds I,: decomposed.forming dispersed '. particles; this was ac-
oompanied by a reduction in hardness and an increase in the volume and pla-
sticity,of the specimen. Decomposition of above 400-4500C was charac-
terized by C-curves similar to those of the pearlitic decomposition of super-
cooled austenite (Fig. 2), but the start of i~ separation had not the cha-
racteristical C-shaped line, for some amount of 4 '1 transformation took
place even at very rapid heatirg (up. to 3000046ee, in alloys with a , -composi-
tion close to critical electronic concentration). The high-hardness stage
Card 2/8

22937
S/125/61/000/006/001/010
Investigation of ageing processes D0401/D112
passed very rapidly when the ageing tempo-ature was sufficiently highl thus
hardness decreased during isothermic soaking at 6000C, No sufficient homo-
geneity was obtained by heating to 8000C, for quenching, for this temperature
is near the upper limit of the biphase (t)( + B range. At 9000C homogenation
is already possible, and the ~ -phase becomes less alloyed and decomposes
faster in againg. Contrary to the opinion of some foroign atithors, it had
previously been concluded by Soviet authors that at a certain electronic
concentration in ~ the a-+L) transformation is without diffusion, and that
the reverse martensite-like transformation (also diffusionless) could not
be suppressed even by heating at a rate of several thousand degrees per se-
cond. This cannot be compared with the "reverse" in Co-Al alloys. The
initial transformation in alloys whose A -phase structure has a near-criti-
cal electronic concentration must be presented as shown by the dotted line
in Fig. 5, and not as it is presented usually. In alloys with omega already
Dresent after quenching,the initialil.--) ~) transformation line will be the
same. As it is not possible to fix precisely the start of decomposition
in the case of furnace heating, the specimens were heated by electric resist-
ance in a high-speed dilatometer. They were heated for I - 1.5 see, then
soaked for 90 sees. The results show that no transformation took place in
Card 3/ 8

22937
S/125J61/000/006/001/010
Investigation of ageing processes D040/D112
VT6 alloy, i.e. the specimens' length decreased only slightly, but in the
No. 1 and No. 2 alloys the transformation was sharp and without any incuba-
tion period. It is important from the practical point of view to know 'the
boundaries of the temperature range where the ~. phase exists. The obtained
data indicate that for the VT6 it is 180-4200.', and for No. 1 and No. 2 -
180-4400',, Seen under an electron microscope, the t particles were mo~t-
ly round. The included photomicrographs show no '., in No. 1 alloy welds
after quenching (Fig. 79 a) (hardness was Ev 300-320); the No. 2 had a
slight quantity of .~ and high hardness (Hv 400). After.1 hr ageing at 3500C
both allRys had clear round Aj :-phase particles 300-500 A in size. Elongated
500-800 X long particles were more rare. It is possible that they formed
later, when the particles were only slightly growing. Long ageing ends with
full tranSformation into alpha. In general, the data.show that the quench-
ing temrarature should not, be above 9000C as this reduces the plasticity of
weld metal both after quenching as viell as after ageing. Brief ageing of 2
preliminarily quenched specimens raised the ultimate strength to 130 kg/MM
and considerably docreased the plasticity. Long ag-Ang improved the plasti-
city of weld metal and only slightly decreased the strength, i.e. to 120 kg/
mm2. Conclusions. 1) The decomposition process of the metastable A -phase
Card 4/8

S/125/61/000/0061/001/010
Investigation of ageing processen D040/D112
in hardened welds of VT6, No. I and No. 2 alloys ha:. b,-,,.,n invcotigated. The
transformation kinetics of 9 in ageina of quenched welds in biphase tita-
nium alloys is analog-ous with the 3 -decomposition in the weld metal and
heat-affected zone after -welding. The ageing process is faster in hardened
welds than in vields not subjected to preliminary heat treatment. 2) Dia-
grams of metastable ~ -phase decomposition have been plotted for the No. 1
and 2 alloys, and the decomposition mechanism discussed. 3) The rj ---p W
transformation rate upon ageing of weld metal depends on the temperature of
the preceding quenching. Lowering the quenching temperature from 900 to
80006 speeds up the ageing process in the VT6 alloy. In the No. 1 and 2
alloys the effect is opposite. '4) VT6 alloy welds are less prone to ageing
than welds of No. 1 and 2 alloys9 both after welding and afier quenching.
5) Omega particles forming in the weld metal upon ageing arg round, peldom
elongated. Their respective size is 300-500 1 and 500-600 A~ 6) Quenching
and subse uent long ageing of VT6 welds give an ultimate strength of up to
120 kg/mz~ and satisfactory plasticity. There are 7 figures, 1 table and
17 references3 7 Soviet-bloc and 10 non-Soviet bloc, The fbar latest references
to English-language publications read as follo-,;s; F. R. Brotzen, E. L.
Harman ~.nd A. R. Trolano, Decomposition of Beta Titanium,
"Journal of Metals,
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22937
S/125/61/000/006/001/010
Investigation of ageing processes o.. D040/Dll2
v.7t No. 2, 1955; F. R. Brotzen, E. L. Harmon, A, 141. Troiano, Trans. ALME,
v. 203, 1955; R. T. Jaffee, Frog. Metal Phys., 7, Revue, 1956; 1. Y.
Silcock, An X-ray &amination of the Phase in TiV, Tilo and TiCr Alloys,
"Acta Metallurgical', N0.7, 61 1958-
ASSOCIATIONi Ordena Trudovogo Krasnoeo Znameni Institut olektrosvarki im.
Ye. 0. Patona All USSR (Institute of,Electric Welding "Order
of the Red Baw-Ler of Labor" im. Ye. 0. Paton AS UkrSSR)
V. F. GrAbin, S. DI. Gurevich); Institut metallofiziki AN USSR
Inztitute of Physics of Metals AS UkrSSR) (V. A. Rafalovskiy,
~
V. I. Trefilov)
SUBMITTEDs January 249 1961
Card 6/ 8

S/03 61 027/002/018/026
B134YB20~
AUTHORSt Minakov, V. N',_~~
TITLE: Instrument for studying martensite transformations
PERIODICAL: Zavodekaya laboratoriya, v- 27, no. 2p 1961t 207-210
TEXT: An instrument for studying martensito transformations is described.
It permits a determination of temperature duitng heating and cooling, the
elongation of the sample, the potential drop ii., the sample, the amperage
which passes the sample, as well as the taking of microfilm pictures of
the sample surface during direct and reverse martei.qite transformations.
A block circuit diagram of the instrument is given in Pig. 1, (1) being
the time-limit relay, (2) the hardening mechanism (samp:1, cooling with
argon)o (3) the electronic dilatometer (A.- P. Rudoy oooper..ted in its
elaboration), (4) electronic shielding of the loop osoillosk.ipe, (5) a
ferroresonance stabilizer, (6) sample, (7) MA -6 (MD-6) bridg--4, and (8)
the dilatometer pickup. For studies of phase transformations at a rate of
heating above 1000-1500OC/sec, the current frequency of the heater current
Card 1/3

S/032/61/027/002/018/026
Instrument for studying martensite... B134/B206
of the sample is raised. The resistance stability of the thermocouples
is maintained by a slide wire, and controlled by the MD-6 bridge. The
maximum error in temperature measurement is �80C when an mno-2 (MPO-2)
oscilloscope is used. The dilatometric curve is obtained by means of a
differential capacitance pickup which is connected to the anode lines
of two generators with 6M1511 (6N15P) tubes. Through the capacitance
variation of the pickup, the natural frequency of the generators changes
and, thus, the anode currents of the triodes. A loop oscilloscope is
connected between the anodes of the triodes, and records the difference
of the anode currents of the generators. The potential drop in the
sample during heating is recorded by a loop oscilloscope which is shielded
by an electronic block. The voltage is fed to a rectifier (AN-27
(DGTs-27)tube). For various rates of heating, the maximum heating
temperature is adjusted by a time-limit relay which contains a
TP 1-0111.3 (TG1-01/1.3) thyratron and an STV 280/80 stabilizer-divider.
If the sample is to be hardened immediately after heating, the hardening
mechanism is automatically switched on, and argon blown onto the sample
whereby a cooling of 300OC/sea can be attained. Long-focus objectives
Card 2/3

S/032/61/027/002/018/026
Instrument for studying martensite ... B134/B206
of the types OCej-16 (OSF-16) (from the M-BT-(MVT) microscope) and
"gomall III' (from the MOM-8 (MIX-8) miarosoope) were used for taking
microfilm pictures. MagnIfication was 250X for pictures taken with a
KC -:506(050B) camera, and 64 pictures per second could be taken. An
GKC,-l (SKS-1) bovie camera.was used for up to 4000 frames/see. Some
motion pictures of martensite transformations are mentioned in a paper by
V. N. Gridney and V. I. Trefiloy (Ref. 1). A vacuum of io-3-2xio-5 mm Hg
is maintained in the vacuum chamber containing the sample in order to
prevent oxidation of the sample during heating. There are 6 figures and
6 Soviet-bloo references.
ASSOCIATION: Institut metallofiziki Akademii nauk USSR (Institute of
Physics of Metals of the Academ
y of,Science's Ukr SSR)
7
Card 3/3
Nil

S/601/62/000/014/011/01
100311203
AUTHORS: Gridney, V. N and Trefilov
TITLE: A new metastable pM.~e_in alloys of transition elements (fl-phase)
SOURCE: Akademiya nank Ukrayins'koyi RSR. Instytut metalofyzyky. Sbornik nauchnykh rabot.
no. 14. Kiev, 1962.Voprosy fiziki metallov i metallovedeniya. 5-25
TEXT: The present article is the first attempt to generalize all available data on the mechanism and on the
kinetics of the P - (j) trans formation and on the physical properties of these phases. Titanium alloys con-
taining transition metals are widely used, but if the a.-pbase is present the alloys are of little practical value
because the a)-phase makes them highly brittle. It is emphasized that the a)-phase is an electron compound
and that the fl - w transformation is a diffusionless one of the martensitic type taking place at constant values
elect ron-to-atom ratio. The authors take issue with the opinion expressed by certain Western scientists who
consider that the formation of the co-phase in the matrix of the overcooled #-phase is a result of diffusion
processes. The formula G b
as=A r VP
shows the relationship between the shearing stress required to cause the crystall planes of an alloy to slip,
and the amount and dispersity of the w-phase in the #-phase matrix. The behaviour of the #-phases under
different conditions and the mechanism of the plastic deformation of semiconductors are discussed. There
are I I figures and I table.
Card 1/1

S/601/62/000/015/010/010
A004/A127
AUTHORSt Gridnev, V.N., Lotsko, D.V., Trefilov, V.I., Chernenko, N.F.
TITLE: On'the nature of changes in the physical properties of titanium al-
loys in the temperature range of 100 - 400 C
SOURCE: Akademiya nauk Ukrayinslkoyi RSR. Instytut.metalofyzyky. Sbornik
nauchnykh rabot. no.-15- Kiev, 1962. Voprosy fiziki me~tallov I
metallovedeniya, 192 200
TEXT: The-authors investigated phase transformations in titanium alloys
containing additions of 2:3 and 5 weight % Al, 1.87 and 5 weight % Cr, 2.2 and 5
weight % Fe, 3 and 5,weight % Sn and also iodide tttanium and titanium of commer-
cial purity'- grade BT-1 (VT-1). The alloys were melted in an are furnace and
by the Induction drop-melting method in purified argon with triple remelting.
They had the shape of bars 3.5 mm In diameter. Plastic deformation was effected.
by drawing. The degree of deformation was determined as the relative reduction
in cross section. After processing under various conditions, the specimens were
subjedted to x-ray, dlectron-diffraction and electron-microscopic examination.
Card 1/2

S/601/62/000/015/010/010
On the nature of changes in the physical .... A004/A127
The authors give a detailed report on the test results and come to the conclusion
that the cause of the anomalous volumetric changes in titanium alloys in the tem-
perature range of 100 - 400.C is the hydrogen ageing,which is considerably accel-
erated by deformation. According to available data (Tien-Shiuh liu, Morris V
Steinberg. Trans. ASM, 50, 455, 1958) the crystallographic planes of hydride sep-
aration are (1010), (1011), (1121) and (1012). These planes coincide with the
possible,glide planes and twinning planes in OL-titanium at room temperature,
which increases 'the sensitivity of the alloy to impact loads and causes an in-
tense hydride separation in alloys subject to considerable plastic deformation.
There are 7 figures and 2 tables.
SUBMITTED: June 25, 1961
Card 2/2

S/601/62/ooo/oi6/002/029
Elll/E451
AUTHORS: Millman, Yu.V., Trefilov'_ V.I.
TITLE: Contribution ~n the brittle transition temperature of
metals with a body-centorad cubic latti!ce
SOURCE: Akademiya nauk Ukrayins'koyi RSR. Instytut metalofyZyky.
Sbornik nauchnykh rabot. no.16. Kiev, 1962. Voprosy
fiziki metallov i metallovedeniya. 16-21
TEXT: The authors apply a mathematical treatment of dislocation
theory to calculate the brittle tran3ition temperature Tx for
low-carbon steel and cast molybdenum. Their results agree well
with experimental results for both materials. However, for
considerably smaller block sizes calculated results are low.
An increase in the speed of deformation from 10-4sec-I to 102sec-l
causes Tx to rise, the absolute increase (which can exceed 2000C)
being much greater for molybdenum than for iron. This explains
the profound effect of test conditions on the Tx values for
molybdenum and the fact that its notch sensitivity is higher than
that of steel. A decrease in grain size reduces Tx more in
molybdenum than in steel; decrease in substructure size and
Card 1/2

S/601/62/000/016/002/029
Contribution on the brittle E111/E451
increase in di5location density reduces Tx for both materials.
It is confirmed that by varying the substructure it should be
possible to vary the transition temperature over a wide range.
There are 2 figures and 2 tables.
SUBMITTED: January 27, 1962
Card 2,,Z

sAol/62/000/016/001/0219
E-193/F,383
AUTHOR: Trefilav, V.I.
-TITLE- Is ocation theory of brittle fracture
50UPCE: Akademiya nauk Ulcrayitialkoyi R5R. Instytut metalofyzy1c);
Sburnik naucliny1ch robot. no. 16. Kiev, 1962.
Voprosy fiziki metallov i nietallovedeniya. 3 _ 15
TEXT: A general equation for brittle fracture was obtained
and found to be a special case of Stroh's equation. The solution
of this equation yielded a formula:
o, - 0.75 K e-1/2
0
T (16)
N1
x )1/2~
In
d
where T is the ductile-to-brittle transition temperature, tile
strain rate, d grain size, the size of the mosaic blocks and
K, and IN' are constants; the stress o~ is a measure of
0
Card 1/2

I/ 62/ocac/c Its/ oc; 1/0
Dislocation theory .... F 19 3 / F-.-> 63
a (1, 1,) c,-, t i o ti surrouricl izi~,
tj-,0 force cif illtol-tIctictj J)etwr,(~,n ri -In(] le
:6--irwrities and represerits tho comt-)mionts
of the yield st-r(?..gs. The rcle.Lionship betaeen I/T and lo~- d
obtained from fon--iula (It-)) shculd be line-ar if all the other
f a c t o r --; a L-,~, c o ns t an t ;t h is Ib c ~ c- 11 criiiFirrued experiuientally for
ti"ro Steels. The validity of (11,~ 1-rLis aLso carifirmed by
oxper-imental data on the relition~,hi--, botween F- a n (11 1 /T It has
been .5hov,-n that T is affect(-d by ~;,-clirninary plastic defornation
of st eel ; this effect has boc,li 'Ati-Lbuted to the effect of
preliminary trecktment on the substru,;ture of the material. It i,.,a5
concluded thiat furth er studj-' e~~ on th a !3,ibj ect should entail more
rigorous analy-gis of the conCitions --nd riechanism by 'uhich dis-
locations ara removed frout th"411- lores and calculation of
'the activation energy for th(! iatter Pr;)Cess. There are 5 fi3ures
and I taole.
-B' 19G2
5
1) MITTED: January 27,

f
DRACHINSKly A.S.; MOISETEV, V.F.; TREMOV, V.I.
Conditions of the start of flow and the failure of iron.
Sbor. nauch. rab. Inst. metallofi~. AN URSR no.18-.18-21
r64 (MIRA l7z8)

111111AKOV, V.N.; TRE?TLOV-, V.I.
Speatrometrf-. rasolutfon
of a �m
recording of eoi4, X ray;s. Sbor. naueh. rab. Inst. matallo-
fl--. AN URSR no.18t220-2271* 20,',

GRIDNEV, V.N. [Hrie-niev, V.11.1; MINAKOV, VA.; TREFTLOV, V.I.
Auatenite formatirin in quAck houting of' ntPhl. Rr. Nz.
zhur. 9 no.3,318-324 Mr '64. (MMA 17:9)
1. Institut metallofiziki AN Ukr6SR, Kiyev.

- ~ 0,0-
- --- --, m ~7
, 4p - J- .
i-_ "-;- -:--- -~ I , -
,-' '-'Vvla .-.1
~-. a, -,-- i;l,
C ~7

Tt wis
;4ria rnE

HILIMMY Yu.V.; T111FILOV, V.I.
-14 ~ -, ~...... a.-
Temperature of cold brittleneso. Ukx. fiz. zhur. 9 no.7:792-794
i1 164. ("aia 1-1: 10)
1. Institut meta:Llofizild AN UkiOSR, Uyev.

24470-66 EWT
M ft/EWF~M
'ACC NR: AT6010573 (N) SOURCE CODE: UR/0000/65/000/000/0042/oo5q
`AUrHOR: Dmrachinskiy, A. S.; Trefilov, V. I.
:0
RG: Institute of Physics of Metals AN UkrSSR (Institut metallofiziki AN UkrSSR
1TITLE: Transition from intercrystalline to tienscrystalline fracture in molybdo
ASOURCE: AN.UkrSSR. Mekhanizm plasticheskoy deformatsii metallov (Mechanism of the
plastic deformation of metals). Kiev, Naukova dumka, 1965, 42-53
-TOPIC TAGS: molybdenum, material deformation, material fracture, grain size,
phase transition
'ABSTRACT: The transition from intercrystalline to transcrystalliqe fracture is i
istudied in molybdenum specimens produced by electron-beam meltin ith subsequent
iextrusion and forging. Tensile tests were done at :mom temperature at a deformation
rate of 1.3-10-2/cm. An oscillograph was used for recordi ng the tensile diagrams j
band the state of the fracture surface was studied uader.an optical microscope. A
!graph is given showing the true breaking stress as a function of grain size. The
Icurve shows a sharp departure from the linear relationship fte'll, at 3
e ti ile
A transition to brittle fracture is observed at the sam me on-the tens
Card, 1/2

6"
-L,2447046
~.:.'ACIC NR: AT601OS73-
Idiagrams. Microstructj analysis also shows a change in the nature of the trac-
ture. 'A transition is, observed in the region d-lly--,- 3 aAr"112 from transcrystalline fra6-
ture (at d-112> 3 Auf-112) to mixed, and finally (at d-il ~z 3 - 1,2 mAr'12 ) to fracture
ialong grain boundaries. The experimental results indicate that considerable plastic.
.'!deformation precedes fracture. It is shown that the tvansition to intergranular
Ifracture is not due entirely to precipitation of brittle phases along the grain
llx)undaries as is the case in the fracture of multicomponent alloys. Some- of the ex-
,1perimental data may be explained on the basis of the Zener mechanism of intergranu-
lar fraicture. According to this model, conditions for development of slippage along
I in boundaries become increasingly'worse with reduction in grain size. A:t the
gra
Isame time, accommodation-conditions improve so that friicture along grein boundaries'
~finally disappears. Models proposed by D. A. Robins and R. C. difkins are also con-
sidered. A choice between the various mechanisms studied is impossible on-the basis'
-'of the available experimental material. Further research in this direction is
.~Ineeded.. Orig. art. has: - 8 figures#
ILSUB CODE., 11,20f SUBM DATE: l4Nov64/ ORIG REF: 009/ OTH REF: 021
V.
~Card 2/2400~

L 2446 -6 EWT(m)/E
Lrc(f) PF(n)-2/B',G(m)/T/EWP(t) IJP(c) ',JD/JG/GS
ACC NR: AT6010572 00 SOURCE CODE: Ult/0000/65/000/000/0029/0041
.;AUTFOR: Millman, Y~. V.; Rachek. A. P.; Trefilov. V. :1. . Ud.ovenko, A. A.; firzLtof L i
~S. A., Yaremchuk. V. V,
-;OFtG: Institute of Ehysics of Metals AN UkrSSR (Institut metallofiziki AN UkrSSR)
JITLE: Mechanism of plastic deformation In alloys of_ ransition metalg-
OURCE: AN UkrSSR. Rekhanizm piasticheekoy deformatsH metallov (K-achanism of the
-:-'P:Lastic deformation of.metals). Kiev, Naukova dumka, 1.965, 29-41
'TOPIC TAGS. plastic deformation, cast alloy, phase tvansition, twinning, material
!fracture
; k (Hilln-m, Yu. V., Trefil
'ABSTRACT: The paper is acontinuation of a previous wor ov,
I., Rachek A P -"Problems in the Physics.and Science of Metals, 2011, Naukova
clumka, Kiev, 1964) devoted to the mechanism of plastic deformation and brittle fraco
;ture of alloys of elements in group VIA with other transition metals. The-following
alloy systems are studied: Cr-Mn, Cr-Ru, Cr-ret Cr-Os, W-.Re$ Ho-Re, Nb-Re and ?4o-TL
Ine alloys were studied in the cast state and in sonxi cases were subjected to heat
-- - - ------- ----

1;,.24469_66
CC NR: AT6010572
A
The relationship between the packing flaw energy and the electronic
treatment
ransition and nontran-
.~,structure of the alloy is analyzed. It is shown that both t
rg.L
sition metals conform to the Seger rule on high ene 'es for packing defects in
nsition in all ys of transition metals is stud-!
.Nmetals. The twinning * slipping tra 0
Aed. All alloys of elements in group VIA with metals in groups VIIA and VIIIA show'
transition to twinning, while alloys with elements in group VIA (Ho-Ti' alloys)
,.show no twinning throughout the entire region of solid solutions with a bee latticel
under maximum loads. Experimental data show that alloying chromium, molybdenum and:
]':tungsten with metals of groups VIIA and VIII reduces the packing flaw energy and
causes a transition.to deformation by twinning (or to combined deformation by
Slipping. and twirwing). A brief survey of the literature shows no transition to
:''.twinning in alloys of-group VIA with transition metals to the left of the chromium
moup in the periodic table* Orig. art.. has: figares4
9
SUB CODE: 11:1. SUBM DATE: 14Nov64/- ORIG REF: 003/ OTH REF: 026
Refract Ing metals
."Card., 2/24411-0---
ACC NR.
-T6009600 (N) SOURCE CODE: UR/OoO/'65/000/ooo/olol/OW
ATJnIOR: GrWnev, Ve
No; Ivashchertko, It. K.. J1~jl1jjj.,jnu
So A.. V.; Trefflov, V. j1,; F
ORG: Institute of Metal Physics, AN Ukr,-,SR (Institut metallofiliki AN Ukr&qSR)
TITLE.- Investigation Oi the effect of highly active elements on the
21asticityof chromium
'SOUIRCE: AN UkrSSR. Fizicheskaya priroda khrupkogo, r 7
azrusheniya metallov (Physical
nature of brittle failure of metals). Kiev, lzd-vo Naukrova duralut, 1965, 101-111
'TOPIC TAGS: chromium, plasticity, metal aging, yttrium, rare earth element
A13STRACT: The article deals with the refin-ing of chromium by treatment with highly active
elqments which react with the interstitial impurities in Cr to form more stable compounds
thap the corresponding Cr compounds. To this end, the use of Y and other rare-earth elements
is ]]aeLicularly promising since then it is often possible to impr_OVO)-~t Only Me plasticity but
alB4 the high temPOratUre strength of the alloy. Howover, there is no common COnsensus on
thiS effect of Y and rare-earth elements. Thus, 0. No Carlson et al. (Less Common Metals,
P
IZ64, 6s 69 439) present experimental findings indicating that the temperature of cold brittle-
Card

L 41026.-66 7
009600
ness of cast Cr increases when It Is treated with Y and other rare-aArth elements. To clear
UP this contradiction, specimens of Cr treated with Y as Nvell as oPS-re Cr in soldered and
evacuated ampoules were annealed at 1200'C for I hr and water-quenched. By means of Vickers
hardness tests, aging of these spealmons was Investigated at three temperatures (2750, 350*
and 400*C) in a molten-tin bath. The firidings on tho increass in microliardness with agring are
presented in Fig. 1, where each point represents the mean of B-10 measurements. Fig. I
f
'-go- /100V
.40 1" - I
M 20 A 11" '6' - '
A
- - %. ", L
I I 1111T I
350 le
" L350EV
40, Fig. 1. Effect of treatment with Y and
0
Pr on the aging of Cr:
W4 0 ff-y-y-HI 1.4
-20
'M 275 0 - zone-refined Cr; alloy of
so. 10
4) W
Cr + 1% Y; A - alloy of Cr + 1% Pr
03
d) 4D
Aging time, min.
2/3

L 141026-66
ACC NR'
AT6009600
indicates that the addition of Y virtually suppresses the processes of"M the alloy (and
hence also it suppresses the rise in the temperature of cold brittlencad &ue to the segregation
of an Interstitial impurity -- nitrogen -- from the solid solution). These findings confirm the
feasibility of using Y to improve the refining of Cr, since Y binds the greater part of nitrogen
into nitrides, thus suppressing most of the effects of aging. Further tests, involving the
treatment of Cr with mieroamounts of Y and Pr over a broad temperature range: from the
temperature'of liquid hydrogen to +900*C, showed, that guch treatment enhances the microhard-
me of Cr t elQyated tempeiutures Orig. art. has: 5 figures.
SUB CODE: 13, 11, 20/ SUBM DATE: 120ct64/ ORIG REF: 005/ OTH REF: 026/
3/3

ijp(c) jo
i ACC NR1 AT6026909 SOUACE'CODE: UR/0000/66/000/000/0056/0062
:d%WHOR: Belous, 0. A. Gridnev, V. N.; Yefimov, A. I.; Millman, Yu. V.; Trefilov, V. 1.1
ORG: none
and G- it hromi
TITLE: The effect of annealing temperature on Q 2~~rl d alloys of~
-Yttrium an
chromium with 'i ly~ d gadolinium
SOURCE: AN SSSR. Institut metallurkpii. Vnutrenneye treniye v metallakh i splavakh
(Internal frict on metals and alloys). Moscow, Izd-vo Nauka, 1966, 56-62
TOPIC TAGS: internal friction, annea3Ang, temperattav dependence, chromium, high
purity metal, yttrium, gedoliniuml metallographic w:amination,, grain structure, dislo-
cation affect
ABSTRACT* The effect of annealing temperature on temperature dependent internal fric-
tion was studied in zone malted chromium, Cr + A Y, and Cr + It Gd. Wire samples of
0.8 mm diameter were draim at 3000C to about 95%. These wires were annealed before
testing for 1 hr at temperatures ranging from 100 to 11000C. At low testing tempera-
tures the internal friction in the pure chromium waus twice as low as that in the al-
loys. In all cases, the internal friction decreased as a function of annealing temeera.
ture; in zone refined chRvmium, the internal friction dropped from 15-10-4 to 5-10 4
after annealing to 3000C; in Cr + 1% Y, the internal friction decreased at 500C after
Card 1/3

AT6026909
annealing up to 6000C. These change3 were partially caused by the redistribution of in.
terstitial impurities during annealing. Transmission electron microscopy showed that
the density and distribution of dislocations did not change after-annealing up to 4000(
Thus in the alloys the internal friction decrease was caused by polygonization. Micro-
structures did not show any differences between pure chromium and the alloys that
would account for the internal friction recovery. At high testing temperatures, the
internal friction increased sharply due to grain boundary relaxation. The rise in in-
ternal friction at high temperatures was the same for all of the metals. The shift in
initial rise of internal friction with annealing was caused by a decrease in both dis-
location density and grain boundary area. After annealing at similar temperatures,
the value of internal friction was highest in the alloys, due to the retardation ofjM-
crystallizationl-by alloying. In the 300-6000C temperature range, the change in Q-1
was caused by polygonization in Cr + 1% Y (the recrystallization temperature of Cr-Y ii
above 80010, wbile in pure chromium above 6000C it was due to recrystallization. In-
ternal friction peaks occurred at 9000C in pure chromium at an oscillation frequency
of 2. 8 cps. In Cr + 1% Gd a similar grain boundary ;eak occurred at 960-9700C at a
frequency of 2.1 cps. In Cr + It Y the peak was not observed because alloying with yt-
trium raised the peak Into a higher temperature range. The temperature dependence of
the square of the frequency is proportional to the shear modulus. Deviations from li-
nearity were observed In the same temperature range where the sharp rise in 0-1 was
observed. This change in shear modulus was caused by grain boundary relaxation and lal
Card 2/3

L 04183-67
ACC NRi AT6026909
tice inhomogeneity. The authors express their gratitude to V. G. Evifanov f the
Xnstitute of Metal Pwics, AN UkrSSR for supplying the zone malted chromAum, produc-
ed by three zone paeses. Orig. art. has: 4 figures.
SUB CODE; U,20/ MH DATE: 02Apr65/ ORIG REr: 011/ OTH REF: 008
Card 3/3 1'/-

ACC NR% AP6033049 SOURCE CODE: UR/0126/66/022/00210227/ 0233'_
AV T ~i* P, ; Statkevich V H
110p,: yefimov, A. I,; Kushnareva
iTrefil~ovy
I M_Ib_~
Institute of Physics of Ifetals,,AN UkrSSR Institut metallofizikL
rSSR); Electric Weldtag Institute im. Ye.*O#_Paton, AN UkrSSR
itut
TITLE; Structure sensitivity of plastic propectice,of elect on b2gm-
melted molybdenua alloys 16
_z~ 1-
SOURCIE: Fizika i?metallov i metallovedeniye, v. 22, no. 2, 1966,
227-233
TOPIC TAGSs molybdenum, molybdenum alloy, molybdenum alloy structure,
molybdenum alloyiplaatic'14y, MErqLc^1-5-rt11_
ABSTRACT: Specime'no of electron-beam melted molybdenum and 'Ho-C-Ti
and Mo-B-Ti alloys have been subjected to bending tests In the aa-cast
and annealed (in vacuum at 2000C for I hr) conditions. it was found
that the plasticity of violybdenum alloys depends, to a great degree,
on their structure. Specimens of pure molybdenum and Mo-C-Ti alloy cut
from the ingots along their longitudinal axes had crystals positioned
in the lengthwise direction and they were plastic. As-east pure,
Card 1 / 2 1 UM 548.4

ACC NRt AP6033049
molybdenum longitudinal specimens withstood bending to 180% without
failure, while annealed specimens failed at 150" in a transcrystalline
mapnere Specimens of Ho-C-Ti alloy broke at a 150-160* bending angle
with a fracture along the grain. Specimens of pure molybdenum and
Ho-C-Ti alloy cut across the ingot axis were predominantly brittla and
broke at 0% with the exception of,annealed specimens which brqe at
70-90% All longitudinal and crossectional specimens of Mo-Br-Ti
alloy were brittle, showing predominantly transcrystalline fracture.
It was established that alloys with high plasticity have clearly
developed fragmentation and a disorientation of substructure fragments
of 2-4*. Orig. art. has: 4 figures and I table,
SUB CODRs-.Il/ SUBH DATEj 22Dec65/ ORIG REFs 010/ OTH RE1?i 018

ACC NRi AP7005136 SOURCE CODE: UR./0126/66/022/004/0611/0610
AUTHOR: Trefilov, V. I.; Firstov, S. A.
ORG: Institute of Metal Physics, AN UkrSSR (Institut metallofiziki All UkrSSR)
TITLE: A study of deformation and crack formation in thin chromium foils
SOURCE: Fizika metallov i metallovedeniye, v. 22, no. 4, 1966, 611-616
TOPIC TAGS: chromium, thin film, brittleness, mater! al fracture, electron microscopy
plastic deformation, crystal dislocation, grain structure, C-RAC< RRoP*9c,~9rloA)
ABSTRACT: Electron microscopy was used to study deformation and crack formation in
thin chromium foils. The chromium foils were made from ingots which were arc melted
in argon. Circular, self-supporting samples were made from discs which were gradually
thinned toward the center (thinnest section),.and cracks were induced at the center by
pricking the disc near the edge. This method allowed various stages of deformation as
well as crack formation to be studied. An electron micrograph showed slip traces caus-
ed by the intersection of mobile dislocations with the oxide layer formed by electron
bombardment. These slip traces were identified with surface interactions. Disloca-
tions accumulated in the slip planes along the boundaries of the foil as a result of
retarded motion. Three slip planes were observed: (110), {112), and {123). Aging
the foils at room temperature or heating to 3500C in the microscope Column did not af-
1/2 UDC: Z39.4

ACC NRz AP7005136
fect the microstructures. Electron micrographs were.also given of fractured center
sections of the sample disc. Both intercrystalline and transcrystalline cracks form-
ed. Cracks along grain boundaries did not result in much plastic deformation in neigh-
boring areas. It was hypothesized that these were caused by dislocations moving at
stresses below the elastic limit of the material, accumulating in grain boundaries,
and nucleating as cracks at well below the elastic limit. Interactions of transcrys-
talline cracks with grain boundaries also occurred. Cracks penetrating into the thick-
er sections of the foil.were bent at the point where 'the crack stopped propagating.
This region showed heavy plastic deformation. The slip plane reactions necessary to
fom cracks (Cottrell mechanism) were outlined by slip traces in the foil which ad-
joined the crack edges. Slip planes and directions were given for microcrack nuclea-
tion in the foils. The microcracks *lay along the (1.121 plane and did not have the
orientations necessitated by the Cottrell-mechanism. In utilizing these results in
foils it is necessary to consider the details of deformation in foils, particularly
the stress state and surface effects. Orig. art. has: 5 figures, 1 table, 1 formula.
SUB CODE: 11,20/ SUBM DATE: 09Nov65/ ORIG REF: 009/ OTH REF: 006
Card 2

MILIMAN, YII.V.P-
of
AN URIBR ro.19: 511-53
cryst-nifs. Slx)r.rau,,r;-trlUJ,-j (MIRA 18: 5)
164-

MILIMAN, Yu.V.- RACI-U,',K, A.P.; TREFILDV, V.I.
P
Investigating the mechanism of deformation and brittle failure
of transition metal alloys on a base of the group VIA metals.
Sbor. nauch. trud. Inst. metallofiz. AN URSR no.20:3-24 164.
(MIRA 18:5)

GRIDkFEV, V.N.; IVASflC~,!El4KO, R.E.; IAIILIIMATI, Yu.V.; TP.FFII.JOI,F, V.1.
Plasticity of chromiuln alloyed with yttr4,,rr.. Slbor. nailch. trud.
L
Inst. metallofi.z, AIVU'PSIR no.20:25-31 '64.
(MIRA 18: 5)

LOTSKO, D.V.; TREFILOV, V.I.
X-ra7 study of defects of packing in metals with a body-centered
cubic lattice. Fiz. met. i installoved. 19 no.6:891-898 Je 165.
(KRA 180)
1. Institut metallofiziki A14 UkrSSR.

MILIM.Ally Yu.V.; TREFILOV, V.I.
Nature of the "yleld tvaoth." Sbor.naunh.trud.
AN URSR no.19.-1,6--50 164. (MIRA 18:5)

DRACHINSKIY, A.S.; MOISEYEV, V.F.; TREFIW~
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