SCIENTIFIC ABSTRACT KORNILOV, I.I. - KORNILOV, I.I.

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• Collection: Scientific Abstracts
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• Document Creation Date: November 2, 2016
• Document Release Date: June 14, 2000
• Sequence Number: 9
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT

BI TSIN-YJWA [Pi Ch'ing-hua); KOR111LOV,..I.l '
Phase equilibrium diagram for the syst4m titanium - vanadium -
'iron. Trudy Inst. met. no.8:54-57 161..' (MIRA 14:10)
(Titanium-vanadimm-iron &Uoya.-44etallography)
(a, ase rule and equilibrium)

KORNILOV, I.I.; MATVEYEVA, N.M.
Vanadium and its fields of applieation. Trud3r.Inst. met. no.s: ..
58-81 '61 - - (14W 14:10)
(Vanadium)

.KORNILOV, I.I.j- NARTOVA, T.T.
Dependence of.the creep of alloys in tlw binary system
titanium - t-ib on their composition. Tvidy Inst. met.
iio.8:10A.lo 61. (min w 10)
(Titanium-tin a.Uo7*-4btalIo9r%Yw)
(creep of metals)
(Phw rule.aW equilibrium)

AUTHORSt
TITLEs
PERIODICALR
Pi Ch'ing-hua, Kornilovv I. I.,
5/076 61/006/006/005/013
B 11 OYB206
Phase diagram of the ternary system Ti - V - TiFe
Zhurnal neorganicheskoy khimiiq v. 69 no. 69 19617 1351-1354
TEM From the investigation results of quasi-binary sections TiFe 2 - V
and TiFe V, the authors established for the phase regions of the ternary
system Ti V - TiFe that at room temperatuxe four monophase, five diphase,
and two triphase regions are in a state of mutual equilibrium. It was the
authorO aim to study the phase diagrams of this system at 1000 and 8000C,
as well as the phase conversions of some alloys In the solid state. 93
alloys from titanium sponge 'Tr -0 (TG-O)~ metallic vanadium (99% V), and
an alloy corresponding to the compound TiFe with a ratio Ti 8 Fe - 50 3 50;
60:40; 7000; 8Oa2O; 84,16; 9000 and 950 were produced and investigated
by m1crostructure- and X-ray structural analysis. For the structural 0
analysis these alloys were quenched in water after 46 hr heating at 1000 C
and 248 hr at 8000Co The alloy with 2*5~ V and 4.04, Fe was in the diphase
Card 1/6

23079
!i/07e/61/006/006/005/015
Phase diagram of the ternary system ... 13110/B206
84 : 16 and variable,V' content, on . tl.~e basis of which the polyt hermal
curve (Fi&. 4) was built. It can be seen fr6m it teat the phase conver-
sions change over for % V from the A +.,-,+ ' -regions into the v~ + +
0
region at 600 C at relatively 1 ~ tempe~aiuiea, for 101p V from zhe
0 %
region into the ~ +~'-regionat 505OC-
With.an increase of the V content
above 4Wo, the temperature of the conversion of. the JR, +,,, -phase into the
solid f-l"-solution drops. In all phase conversions from triphase regions
+ into diphase regions, heat is set free, which
determines the conversion temperature. There.are 4.figures, 1 table, and
5 references: 4 Soviet-bloc and 1 non-Soviet-bloc. The refe.-ence to the
~nglish-language. publication reads as follows: W. R. Lucas, W. P. Fizhel.
Trans.Amer. Sqc. Metals, A_6,'277 (1954)-
ASSOCIATION: Institut metallurgii Akademii nauk SSSR im. A. A. Baykova
(Metallurgidal Instituteimeni A. A. Bavkov,* AS USSR)
SUBMITM: -April 30i 1960
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89362
S/089/61/010/002/013/018
B102/B209
AUTHORSt Kornilov, I. I., Polyakova, R. S.
TITLE. Hardness of some alloys on niobium basis at high temperatures
PERIODICAL: Atomnaya.energiya, v~.-10, n. 2, 1961, 170-172
TEXTt The present "Letter to the Editor" deuribes investigations of the
temperature dependence of thelhardness of niobium and of some of its alloys,
which were carried out after a method described in Ref. 1. The alloys
examined had the following composition (in %. by weight):
Nb Mo Zr Si Al a
100
95 5 -
90 5 5
89 5 5 1
Be 5~ 5 1 1
67,8 5 5 1 1 0,2
Card 1/4)

89362
S/089/61/010/002/013/01,3
Hardness of some alloys B102/B209
the investigations: 1).Niobium, just as nickel, iron, or cobalt may be
strengthened by alloying i-t- the components may be introduced either by
Oormalion of a solid solution or by formation of a supersaturated solid so-
lution and separation of the excess phase, 2' The method of the "hot" hard-
ness (which was used here) allows to characterize in first approximation the-
hardness of alloys at 0high temperatures. 3) Multi-component alloys showing*
high hardness at 1000 C have to be further exe,mined and to be tested for
heat resistance by means of standard methods. There are 3 figures, 1 table,
and 3 references: 3 Soviet-bloc.
SUBMITTED: June 18, 1960
g/mm2)
Legend to Fig. 2: Ordinate: Hardness (k abscissa: Temperature (00.
The figures beside the curves indicate the number of component s (cf Table).
Legend to Fig. 3: Strengthening coefficient of the alloys at three dif-
ferent temperatures; the figures ndenote the (n+l)-component alloy.
Card -3

31o5t?
S/126./61/012/004/008/021
E193/E383
AUTHORS: Kornilov I.I. and Yakimova, A.Mo.
TITLE- The effect of h drogen on the structural properties
of alloys T3, TK, T6 and T8
PERIODICAL: Fizika metallov i metallovedeniye, v. 12, no* 4,
1961, 550 - 557
TEXT: The alloys T3, T4, T6 and T8 represent a group of
alloys of the six-component Ti-Al-Cr-Si-Te-B system, differing
in the Al content only, the total conteirt of the remaining all-
oying additions being constant at 1.2 - 1.69'. The Al content
of the experimental alloys was 30% (T3), 4.26% (TO, 6.0% (T6)
and 7.3796 (T8), their oxygen and nitrogen content being 0.09%
and 0-030%, respectively. Hydrogen (0-005, 0-015, 0 025, 0-05
or 0.08%) was introduced by heating in vacuum at 70; 0C in the
presence of titanium hydride. The effect of hydrogen was
studiod by metallographic examination, mochanical testing and
X-ray diffraction. Tensile tests were carried out at room
temperature at strain rates of 0.16, l1.-'; and 48.2 mm/min. The
impact strength was determined at +20 and -78 OC. Thermal
C a: d 1/7~

31052
S/126/61/012/004/008/021
The effect of hydrogen on 2193/9.383
stability (resistance to oxidation) was i3tudied by holding the
alloXs for 100 hours at 450 and 500 (T3 and TU or 500 and
550 C (T6 and T8) and subjecting them to tensile tests at room
temperature. Several conclusions were r,Bached.I)Addition of
up to 0.25% hydrogen slightly increases the room-temperature
tensile strength of the alloys studied without significantly
affecting their plasticity with the exception of the alloy T,-Q,.
This is illustrated in Fig. 2, where reduction of area
vertical scale) is plotted against the hydrogen
content (0,G) and strain rate (v, mm/min) used during the tensile
test. These results were'attributed to the fact that the
la t t i c e of the a-phase was only slightly distorted
by hydrogen owing to its small atomic radius. The loss of
ductility in alloy T8 is most likely associated with the
precipitation of brittle a2-phas'e. 2) The impact strength of
alloys T4, T6 and T8 at room and sub-zero temperatures is not
affected by the variation of the hydrogen content in the
0-005 _-~.08%6 range. Alloy T3 is an exception because of low
Ca3

The effect of hydrogen on
31052
S/1215/61/012/004/OoB/o2i
E19VE383
solubility of hydrogen in alloys with 39/o Al. In the can* of
this alloy, the impact strength at room ".'emperature falls
from 4 kgm/cm2 at 0-005% hydrogen to 1.0 kgm/em 2 at 0608%,:~the
corresponding decrease 2in the impact strength at -78 C being
from 3.2 to 0.8 'xSm/cm . 3) Thermal stability of the alloy
T8 is strongly affected by the variation of its hydrogen contont
which, however, does not affect this property in thecase of
alloys T3, T4 and T6. This Is indicated by data given in
Table 3, showing the vari 'ous mechanical properties of the alloys
studied after preliminary treatment consisting of heating in
air atvarious temperatures for various,limes. 4) X-i-ay ~
diffraction analysis revealed the presence of a residual P-phase
in the alloys studied. The m- and P-phanes are not in equilibriun
and a transformation takes place when these alloys are held for
1.00 hours at 450 - 550 0C, as a result of which the state of
equilibrium is xuached. This transformation is accompanied by
redistribution of the alloying elements between the a- and
P-phases, the P-phase becoming enriched with Cr and Fe.
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3105 2
S/126/61/oi2/oo4/008/021
The effect of hydrogen on oeo E193/E383
5) The lattice parameterof the P-phase in the alloys T3 and
T4 is unaffected by the presence of hydrogen. In the case of
alloys T6 and T8, hydrog3n dissolving in the 0-phase on
heating considerably increases its lattice parameter.
Acknowledgments are expressed to N.I. Blok, A.I. Glazova and
N.F. Lashko. There are 5 figures, 3 tables and 7 references:
5 Soviet-bloc and 2 non-Sovlet-bloc.
SUBMITTED- February 14, 1961
Card 4/ /
/7 Y

owl&o
Z.L7U S/020/61/137/003/016/030
lgjzg~/ QW 165-T B103/B208
AUTHORS: Grum-Grzhimaylot N. V., ~_0rni1~V_,J.1,I.q_,Py1ayevaq Ye. N-t
and Volkova, M. A.
TITLE: Metallic.oompounds in the range of solid a-solutions of
the system titanium-aluminum
PERIODICAL: Doklady Akademii nauk SSSR, v. 137, no. 3, 1961, 599-602
TEXT: The authors proved (Ref. 6: Tr. inst. metallurgii AN SSSR, no. 2,
1957) that in titanium - aluminum alloys (7.5-20 wt% Al) the resistance
to creeping in bending deformation by the centrifugal method rapidly
increases as plasticity decreases. They point out that such a change of
properties in the range of solid solutions of the binary system Ti - Al
could not be explained by conventional methods of metallographic analysis.
The objectives of the present study were therefore the following:
1~ investigation of the range of solid a-solution in the Ti - Al system;
2 determination of the nature of phases appearing in it by measuring the
Hall effect as a function of the composition of the alloys. The authors
have previously proved (Ref. 9: ZhNKh, .1, no. 10, 1957; Ref. 10: ibid,
Card 1/8

21568 S/020/61/137/003/018/030
Metallic compounds in the range of ... B103/B208
31, no. 9, 1956) that the galvanomagnetic effects are related to the
composition of various alloys in a way that salient points and jumps
appear in the diagram oomposition-versus-Hall effect. This phenomenon
can be explained by the fact that the electron states in the outer atomic
shells are changed by applying a magnetic field. This affects the
behavior of conduction electrons and alters the values of the Hall constant.
The galvanomagnetic effects are closely related to the behavior of the
electron components of the outer atomic shells. The state of the outer
shell may be studied with high accuracy on the basis of these effec'u-s.
The character of the chemical bond between various atoms of metallic
alloys may thus be explained. The authors prepared alloys from pure
titanium and aluminum with an Al content UP to 40 wt% by two methods;
1) powder metallurgy by pressing and sintering in vacuo at 600-10000C
for 50-100 hr. 2) melting in the are furnace with a wear-resistant
tungsten electrode. The current collectors were triangular and knife-
shaped at the point of contact with the specimen. They glided along the
polished lateral faces of the sample by means of micrometer screws. Test
method and measuring apparatus are described in Ref. 11 (N. V. Grum-
Grzhimaylo, ZhNKh, 1, no. 7, 1958). Table 1 contains the resultant mean
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21568
S/020/61/137/003/018/030
Metallic compounds in the range of ... B103/B208
values of the Hall constant of the alloys. On the basis of these data,
the authors plotted a diagram of this constant as a function of the
composition (Fig. 1). Two (a and b) jumps from the linear variation of
the Hall constant to another linear variation are seen. These jumps
correspond to: a) the compound Ti Al with 14-3 atom% (9 wt%) of aluminum;
b) the compound Ti3Al with 25 ato;4 (16 wt%) Al. The sintered and the
cast alloys showed the same behavior. The cast alloys were subjected to
homogenizing heat treatment (between 600 and 9000C for 200-350 hr)
immediately after measuring the Hall-constant. The limited range of the
solid a-solution offers considerable difficalties in the presence of two
metallic compounds if the order of variations of the Hall constant has to
be determined& This determination requires an increased precision of
measurement which was achieved by the device applied,here. The authors
conclude from their data that the solid aluminum solutions in a-titanium
exhibit a complicated kind of interaction owing to the existence of the
two compounds Ti Al and Ti Al which apparently have a hexagonal lattice.
6 3
They might result from solid solutions and correspond to compounds of
the Kurnakov type (Ref. 12:. 1, 1. Korniloy, Izv. AN SSSR, OKhN, 19571
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21.568 8/020/61/137/003/018/030
Metallic compounds in the range of ... B103/B208
no, 4,.395). The diagrams of the Hall constant in the range of the y-phase
in alloys with 46.16 atom% (33wt%) to 53-85 atom% 40.0 wt%) aluminum
.0 atom//,, (36.02 wt,.).aluminum. It corre-
show a sharp discontinuity at 50
sponds to the compound TiAl which was detected by other methods of
physicochemical analysis. The equilibrium of the compounds T16Al, Ti 3 Al,
TiAl and the proof of their existence in the'phabe diagram depend on
the kinetics and on the conditions'of their formation which have to be
further studied. The'appearance of'these compounds in the system Ti -'Al
increases the heat resistance of the alloys and rapidly decreases their
plasticity at an aluminum content of more than 7-8 wt~. There are
I figure, I table, and 12 references: 8 Soviet-bloc and 4 non-Soviet-bloc.
The reference to the English-language publication reads as follows: ,
M. Hansen, Constitution of binary alloys, N.Y. London, 19589 P. 139 (Ref. 1).
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(Institute of Metallurgy imeni A. A. Baykov of the Academy
of Sciences USSR)
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5-."410o 12, q 1 25855 S/020/61/139/004/015/025
B103/B2o6
AUTHORSt Kornilov, I* Is, Ustvayeva, No M,.
TITLEs Heat of dissociation of Kurnakov's compounds Ni3Fel Ni3Mn,
Ni3Cr, and Ni3V
PERIODICAL: Akademiya nauk SSSR. Doklady, v. 139, no- 4, 1961, 880 - 883
TEXT: The heat of dissociation is defined as being the temperature of
transition of a compound into a solid solution at the critical transition
temperature. The authors recall that metallic compounds are formed from
solid solutions (so g## in the system Cu-Au$ No So Kurnakov, S.
Zhemahuzhnyy, V. Zasedatelev; ZhRFKhOt Al, 871 (1915))- In honor of their
discover they were called Kurnakov compounds (I. I. Kornilov, Usp..khim
vyp- 9, e1r045(1952)). In publications (especially of the non-Soviet bloc:
F. Rhines, J. Newkirk, Trans. Am. Soo. Metals, _41, 1029, 1953), they are
considered to be the product of a single atomic regrouping connected with
the ordering of the structure in the homogeneous medium, no phase trans-
formation taking place in this case. Although in the systems Ni - Fef
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25855
S/020/61/139/004/015/025
Heat of dissociation of .... B103/B206
Ni - Un, and Ni - Cr,the above-mentioned compounds Ni 3Me are formed from
solid solutions, only a dotted line of the ordering of solid solutions used
to be drawn in their equilibrium diagrams. The phase transformations
mentioned might, however, be accompanied by considerable energy conversions.
In comparing the phase-transformation temperatures of Ni 3Me alloys in the
three systems mentioned with the heat of formation of Ni 3V and Ni3Ti, the
authors tried to gain new knowledge on the nature of transformations in
these systems. They used the thermographic s.ethod by L. G. Berg and V. Ya.
Anosov (Ref. 8: ZhOKh, 12, 31 (1942)) for the determination of the value
of phase transformations of the systems mentioned in the title. This
method 15 based on a comparison of the areas of peaks of differential
heating curves corresponding to the thermal effects in the standard and
the specimen. Iron was used as a standard. The thermal effects of the
magnetic 06--~ ~ and the polymorphous /3 transformation of iron are
known. On the basis of their values, the authors found the relative error
of determination involved in the!method used here, by calculating the value
of one thermal effect from that of the other. This calculated value is
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2~855
5/020/61/139/004/015/025
Heat of dissociation of see B103/B206
compared with the value in the table,# The autt.ore established that the
two compared values of the (3 Fe transformation differ by 2 - 5%, i.e.,
this diffeiLenoe lies within the range of accureicy of the method. Besides
iron, nickel was also used as a standard for the determination of the ther-
mal effects accompanying transformations in the alloys Ni - Mn, Ni - Fe,
and Ni - Cr. The areas of the therdal effects were measured by geometric
integration. Ni Me alloys were.prepared in the are furnace in an argon
3
atmosphere from electrolytic Ni, Fe, Mn, Cr as well as from carbothermic
vanadium (V content 99.8%). On the basis of a chemical analysis, alloys
corresponding stoichiometrically to Ni 3Me were used for the investigation.
They'were subjected tot a) high-temperature-homogenization annealing,
b) long lasting annealing at temperatures beloir the critical transformation
pointt All alloys were annealed at 4500C excei?t Ki V which was annealed at
3
9500C. The thermal effects were measured after annealing for 700, 10001
and 1400 hr. Table I gives the results. The highest value of AR was
obtained for Ni3Cr with 1400 hr annealing at 4'500C (0-41 kcal/g-at). This
value is much lower than the AR values of Ni Ye' Hi Mn, and Ni V. The
3 3 3
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2%5
8 026/61/139/004/015/025
Heat of dissociation of B103/B206
authors presume that the compound forms here vory slowly, and that the
alloy did not reach equilibrium. This problem Ve to be investigated
further. The authors point out the high 6H valule which is considerably
greater than 1, except for Ni 3Cr. The strength of the chemical bond might
be of different nature in alloys annealed for a long time than In solid
solutions. In the alloys investigated, the ordering processes are
obviously linked with the formation of more stable metallic compounds. In
the authors' opinion, they must have independent ranges of existence in the
phase diagram of the system, and two-phase ran,Vs as phase transformation
of first kind. The authors compare the data of Table 1 with the position
of the respective metals in the periodic system. It is concluded that the
6H values of all compounds mentioned are commansurable and increase ~with
the exception of Ni 3Cr) with the distance of the metal contained in the
compound from the position of nickel in the periodic system. Consequently,
a certain dependence of the properties of 'chemical compounds on the
position of the components in the periodic system is maintained. The
strength of the chemical bond in Ni 3Fe, Ni3Mn, Ni 3V, and Ni3Ti is apparent-
ly also determined by the heat of formation (heat of dissociation). it
Card 4/6

3/0, 61/139/004/015/025,
2PB
Heat of dissociation of B103 B2b6
increases with increasing difference of the chemical properties of the
g;
inter4ating metals, and is thus connected with the position of.the reactin
elements'in the periodic-system. Th4 increasing strength of,the chemical
bond in the series Ni Fer Ni.Mnt Ni Or, Ni V, and Ni Ti must be reflexted
3 3 3 3 3
in the mechanical strength of these compounds, which, however, is to be
investigated additionally. There are 4 figures, 1 table, 'and 13 referenceal
8 Soviet-bloc and 5 non-Soviet-bloo. The two references to English-language
pub'lications read as follows: Ref. 6: P. 11jee6h, S. Sykes, Phil. Mag., 27,
No. 185 (1939); Ref. 7: 0.. Kubaschewski,-et. al. Trans.*Farad. Soc., 220
214 (1954). The third one see in tAe body of the abstract'.
-ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk'SBSR
(Institute of Metallurgy imeni A. A.'Baykov... of the Acade
of Sciences USSR)
PRESENTED: March 13, 1961,by I. I. Chernyayev, Academician
SUBMITTEDt February 22, 1961
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29013
S/020/6!/140/004/014/023
9 MID B106/B110
AUTHORS: Kornilov, I. I., and Nartova~ T T.
TITLE: Continuous solid solutions of metallides Ti-,,Al - Ti Sn in the
system Ti - Al - Sn 1, 3
PERIODICAL: Akademiya nauk SSSR. Doklady, v, 140, no. 1961~ 829-831
TEXT; The authors studied the phase diagram of the ternary system
Ti - Al - Sn. For this purpose, the properties of alloys of this system
were investigated, the compositions of which are located in the section
Ti3Al - Ti3 Sn. Thermal; microstructural, and X-ray structural analyses were
carried outs and electric resistance and hardness were measuzed. The
alloys were prepared fromTr-oo (TG-00) titanium sponge (limit of stability
- 38 kg/mm2), and high-purity aluminum and tin. Crystallization and
phase conversion in the solid state were studied in these alloys by
3ontactless thermal analysis in a plant designed by N. A. Nedumov (Ref. 16:
ZhFKh,.jj, no. 1.- 184 (196o)). The phase diagram for the section
T--; Al - T'_ Sn was constructed on the basis of results obtained (Fig. 1).
3 3
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190i)
S/02o/6-,,/14o/004/0I4/023
I I
Continuous solid solutions B106/B110
The alloys cf this section crystallize in the form of mutually limited
solid solutions on the basis of the solid P-aolution of the system Ti - Al
and on the basis of the compound Ti- 3Sn., and form eutect-ic mixtures with
the eutectic voint at 45% of T '3 Sn (- 20j'a' by weight of Sn), on slow
cooling, these mixtures pass over into a continuous series of solid
a(6)-solutiona with phase conversion. At 960'3C~~ the compound Ti 3A! is
obtained by prclonged tempering from the solid a(6)--solutionsof the system
Ti - Al., which,. in turn-, forms solid solutions with the comround Ti 3Sr.. In
this state, the alloys of the sectiod Tj.,Al - Ti;kSn form continuous Isolid
solutions with hexagonal crystal lattice.. The alloys s*udied exemplify a
complicated phase equilibrium which considerably varies with temperature
and conversions in the solid state. The above-menticned formation of the
continuous series of solid SolUt4ons 'n long-tempered alloys may be
regarded as a continuous replaaemert of tin atoms in the Ti 3Sn crystal
lattice by aluminum atoms without change in the lattice type. There are
3 figures and 16 referen,~es; 10 Soviet and 6 non-Soviet. The three
most recent ref erences to English-language pub'2 icati ons read as f ollows;
Card 2A _-3

29013
S/020/61/140/004/014/023
Continuous solid solutions ... B106/B110
E. Ence, H. Margolin, J. Metals, .2, N2 4, sect. 2, 484 (1957); D. Clark,
J. C. Terry, Bull. Inst. Metals, J, 116 (1956); P. Pietrokowsky, E. P.
Frink, Trans. Am. Soc. Metalsq A2, 339 (1957)-
ASSOCIATION: Institut metallurgii im. A. A. Baykova Akademii nauk SSSR
(Institute of Metallurgy imeni A. A. BayYov of ihe Academy
of Sciences USSR)
PRESENTED: April 20, 1961' by I. I. Chernyayev, Academician
SUBMITTED: March 27, 1961
Card 3/4-3

VOLj Abram Yevgenlyevich; AGEM, N.V., red.; ABRIKOSOV., N.Kh., doktor
khim.nauk, red.; KORNIIg, I,_j,,,-doktor-khim.na:uk.. red.;
"-~Wiim.nauk
SAVITSKIY, Ye.M... o or , red.j OSIPOV., K.A.,, doktor
tekbn.nauk.. red.; IGUSEVA, L.Na., kand,khim,naulc, red. ;
MIRG&WVSKAYA, M.S., kand.khim.naukp red,; SHKLOVSKMA., I.Yu.,
red.; MURASHOVA, N.Ya... tekhn.red.
[Structure and properties of binary meta3-Uc systems] Stroenis
i svoistva. dvoinykh metallicheskikh sistem. Pod rukovodstvom N,V.
Ageeva. Moskva, Fizmatgiz. Vol.2. [Systems of vanadium, bismuthp
bydrogen., tungsten, gadolinium, gallium, hafnium, germaniump holmium,
dysprosium$ europiums iron] Sistemy vanadiia, vismutaj, vodorodap
vol'fr,qmP,, gadolixiia, galliia., gafniia,, germaniia., gollmiiag dispro-
ziial evropiia,, zheleza. 1962. 982 p. (MIU 15:5)
le Chlen-korrespondent AN SSSR (for Ageyev).
(Alloys) (Systems (Chemistry)) (Phase rule and equilibrium)

VULIF, Boris Konstantinovichp dots.,AfOktor tekhn. nauk; ROKAHDIN,
Konstantin Platonovich, dots.) kand. tekhn. nauk; DUDDIIII,
G.N., kand. tekhn.naukp retsenzent;JORVILOV, I-J., prof.,
red.; VINOGRADSMA, S.I., red. izd-va; PUKHLIKOVAN.A.,
tekhn. red.
[Structure and properties of aircraft metalslAviatsionnoe
metallovedenie. 2. izd.p perer. i dop. Pod red. I.I.Korni-
lova. Moskva, Oborongiz, 1962 ' 503 OIIRA 15:11)
(Steel alloys). (lionferrous alloys~
(Airplanes-41aterials)

39076
S/180/62/000/003/011/ol6
E193/E383
AUTHORS: Kornilov, I.I. and Yakimova, A.M.- (Moscow),
TITLE: Creep'and structure of alloys of the titanium-
oxy-gen-hydrogen and titanium-aluminium-hydrogen
systems
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye
-tekhnicheakilch nauk. Metallurgiya i toplivo,
no. 3, 1962, 88 - 93
TEXT; Since most Ti alloys contain'H, 0 and Al (the,first
two as impurities, the last,as-the main'strengthening alloying,
addition;', the effect of these elements-on the.atkucture and
creep-resistance of Ti was studied. The composition (wt.%) of
the experimental alloys varied within the following limits:
o.1-1.630% 0, 0.005-0.05% H and 1.05-7.86% Al. Creep tests were
carried out at 500-550 on the Ti-O-H alloys and 2t 500 - 650 0C
on the Ti-Al-H alloys. under a stress of 7 kg/mm in the former
and 15 kg/mm 2 in the latter case; the results, correlated with
the results of metallographic examination. led to several
conclusions. 1) The creep resistance of Ti-O-H alloys decreases
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Creep and structure ....
3-07
S/180/62/000/003/011/oi6
;9193/E383
with increasing H content, oxygen having 1he opposite effect.
Thus, for instance, the deformation of specimens containing
1 0.025 and 0.05% H after 5 h at 50 0 0 un er a
0.10~ 0 and 0.005.2
stress of 7 kg/mm was, respectively, 10, 29 and 48 min; the
corresponding*figures for alloys containing 0.0511a H and 0.1, 0.2
and 1.25/6 0 being 48, 20 and 1 min. 2) As the 0 content of Ti --
increases, the solubility of H in the metal decreases. In
addition, a change in the v content brings about redistribution
6f h between the a- and y-phases- 3) The creep resistance of
the Ti-Al-H alloys also decreases with increasing concentration
of H, the deformation of alloys containing 37; A! with 0.0052 0,025
and 0.055a' H after 50 h at 500 OC under a stress of 15 kg/mm
being 15. 25 and 35 mm. Increasing the Al content to 5% (or
more) increases the high-temperature strength of the alloy and
decreases the harmful effect of H t~e deformation of alloys
(after 50 h at 500 OC under 15 kg;mm ), containing 8% Al with
0.005, 0.025 and 0.05% H,bting; respectively, 2, 3 and 4 min,
4) As the Al content of th" Ti-Al-H alloy inereases,'the solu-
bility of H also increases from 0.025% at 3-1/4 Al to 0.05% at 5% Al.
SUBMITTzo October, 17, 1960
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1072h
s/18o/62/00o/oo4/oo4/ooq
E040/E435
AUTHORS: Ko-Chih-Ming,, Kornilov, I.I., Pylayeva, Ye.N.. (Moscow)
TITLE: Investigation of the structure and properties of
titanitim-aluminium-molybdenum alloys
PERIODICAL: Akademiya nauk SS 'SR. Izvestiya.-Otdeleniye
tekhnicheskikh nauk. Metallurgiya i toplivo,
no.4, 1962, n4-ii&
TEX7: Using the hot-hardness techniqub for a rapid assessment
of the alloy properties as a function of temperature, an
examination waB made of the hot-bardness and.creep of titanium-
corner alloys of the Ti-Al-Mo terneiry system along sectiqn3
parallel to the Ti-Mo side of thb concentration triangle at
aluminium contents of 0, 5, 10, 15, 20 ana 36% and at molybdenum
contents from 0 to 10%. The testis were made in 'BA14-IM (VIM-11M)
vacuum machine. The test specimens were melted in an are-furnace
with a non-consumable tungsten electrode in an argon atmosphere
and were vacuum-annealed at 11000C for 24-hours, then annealed
again for 24 hours at 6000C and finally cooled with the furnace.
The hardness (1 kg load) was determined in the interval 20 to
lOOO*C (in 1000C stages) after a holding timeofl minute. The
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S/180/62/000/004/004/009
Investigation of the structure E040/E435
hardness of titanium and of its alloy with 5Y6 Al dropped
progressively with rising temperature, whereas the hardness of
alloys with 10, 15 and 20/o Al changes little up to about 700 to
8oo0c. Molybdenum additions have a much less beneficial effect
on the.hardness of titanium, espec4Lally at high temperatures:
the hardness of binary titanium alloys with up to 5116 ko decroased
with rising temperature. The hardness of titanium remained
unchanged as the temperature increased to 500 to 6oo*c if the
molybdenum content was raised to 10776. Studies of the effect of
molybdenum additions on the har Idness of Ti-Al alloys showed that
the hardness at room temperature rises when the Mo content is from
3 to 10%; at higher temperatures the hardness drops. The creep
10
of the alloys was examined at 7000C using a method described
previously (Osipov, K.A., Vien-te-Cheng. Izv.AN SSSR.OTN. M I T.,
no.4, 1959). Molybdenum concentrations up to 1- 3% increase the
resistance.of titanium to plastic deformation at 7000C but this
effect disappears almost completely If the molybdenum concentration
is raised to 10%. In ternary Ti alloys (with 5, 15 and 20% Al),
the highest heat resistance at 7000C was observed in alloys with
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40725
s/18062/ooo/oo4/005/009
E071/E133
AUTHORS: Kornilovq 1.1*j and Yakimova, A.M. fm6scow)
TITLE: -diWe'-p and structure of titanium-chromium and
titaniumrmolybdenum alloys containing hydrogen
PERIODICAL; Akademiya nauk SSSR. Izvestiya.'Otdeleniye
tekhnicheakikh nauk.. Metallurgiyet i toplivo, no.4. 196i,
119-125
TEXT: Since chromium and moly-bdenum enter the composition of
many heat resistant titanium alloys, the creep and structure of
Ti-Cr-H and Ti-Mb-H ternary systems was investigated. The alloys
were prepared in a laboratory arc furnace with a tungsten e'lectrode
in an atmosphere of purified argon, Specimens used were in the
form of hot rolled rods 8 mm in dietmeter. Before.saturation with
hydrogen, all specimenswere vacuo treated (10-4 mm Hg) at 700'*C
for 24 hours and cooled with the furnace. Saturation with hydrogen
at 700 OC for 10 hours and cooling with the furnace. The specimens
were tested for creep by the centrifugical method..directly after
hydroger; saturation without any additional heat treatmept. The
chemical composition of alloys investigated is given (Cr and Mo
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Creep and structure of ... S/180/62/000/004/005/009
E071/E133
from 0.5 to 30%). The microstructure of the alloys was studied by
metallographic and microhardness methods. on the basis of the
results obtained it was concluded -that: 1) Hydrogen decreases the
resistance to creep of alloys containing from 0.5 to 15*,Q' Cr.
2) With increasing chromium content from 3 to 75 the solubility of
hydrogen in titanium increases from 0.05 to 0.5%. 3).In titanium
alloy containing 7% Cr, hydrogen strengthens both the a and p
phases.; At 15% Cr the microhardness of the 0 phase decreases with
increasing concentration of hydrogen due to the decomposition of
the p phase and its impoverishment in chromium. 4) The resistance
to creep of alloys of titanium with 3 and 10% Mo decreases strongly
With increasing hydrogen content. On increasing the Mo content in
alloys up to 20 and 300,1, their resistance to creep increases.
5) The solubility of hydrogen in titanium increases with increasing
molybdenum content.
There are 5 figures and 2 tables.
SUBMITTED. October 17, 1960
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3 66- " 4
S/062/62/000/004/003/013
B110/B101
I Y00
AUTHORSt and Polyakova, R. S.
TITLE: Study in the field of metal chemistry. Communication 3.
Metallochemical properties of niobium
PERIODICAL: Akademiya nauk SSSR. Izvestiya. Otdeleniye
khimicheskikh nauk, no- 4, 1962, 565-573
TEXT: Niobium takes an intermediate position if the elements of the
periodic system are arranged according to their electronegativity.
36 metals are electropositive, and nearly 40 are electronegative as
compared with Nb, which explains its tendency of forming solid solutions
with metals of similar electronegativity, and metallic compounds with
elements of different eleotronegativity: (1) Nb forms a continuous series
of solid solutions with metals whose atomic radii do not differ from its
by more than 6-10., and whose electronegativity is.similar. (2) The
formation of continuous solid solutions requires an isomorphous crystal
structure of the components. (3) Limited solid solutions are formed with
differences in atomic radii of 8-10 to 15-1 Vi and with slightly varying
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S10621621000100410031013
Study in the field of metal ... B11O/B1O1
electronegativity. (4) The greater the.difference in electronegativity,
the greater the tendency of forming,compounds. The metals P-Ti, O-Zr,
V, Ta, Pap Ma, W, and U constitute the first family of elements
forming a continuous series of solid solutions. The second family
(Bep So# Yj Lap Acp Hfp Thp Ort Mnp Top Ret Fe, Ru, Os, Co, Rh, Ir, Ni,
Pd, Ptj Cup Ag, Au, Zn, Od, Hg, B, A1j,qaj In, TI? C, Sip Go, Sn, Pb, N,
P, As, Sb, and Bi) and 10 elements of the actinoid group (altogether
68 elements) form limited solid solutions wi'th Kb. The more electronegative
the alloy metal compared with Kb, the more compounds are formed. The
-third family (S, Sep Te, Fo. F, Cl, Br, 1, and At) forms, with Nbt only
compounds with covalent or ion bonds. Some of these compounds have semi-
conducting properties. An intermediate position is taken by 0, N, Bf C,
and some other metalloids which, according to their reactions with Nb,
belong to the second family but form, with Nb, nome compounds with
covalent bonds. The fourth group consists of elements that do not react
with Nb (Li, Na, K, Rb, Cs, Fr, Mg, Ca, Srp Ba, and Ra) and inert gases
(He, Ne, Ar, Kr, Xe, and Rn). The metals of this group are more
electropositive.than Nb, and differ very much in the ionic radius from
the latter. Metal systems with a given number of elements can be well
Card 2/3

XORKLOVI, 1. 1. (Moskva); NAMVAL,, T. T. (Moskva)
Streos,~ture strength at 7001D in allOYN on, a Ti Al compound
bass. Izv. AN SSSR. Otd. tekb. nauk. Hot. i topl. no.6:142-146
N-D 162. (MIRA 16:1)
(TitwAuw-ainainan anays-Testing)
(metals at high temperatures)

3/598/62/000/007/001/040
D267/D307
AUTHOR: Kornilov, I. I.
TITLE. Metal chemistry of titanium alloys and the further.
tasks of research
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Titan i yego
splavy. no. 7, Moscow, 1962, Metallokhimiya i novyye
splavy, 5-25
TEXT: In view of the ever increasing significance of titanium al-
loys in engineering a detailed survey of this field is given.
There are in all 17 elements (groups 0, Ia and lIa, except Be)
which do not form solutions or compounds with Ti; 9 elements
(groups VIb and VIIb, except oxygen) form with Ti many compounds,
characterized by ionic or covalent bonds; 415 elements (including
groups Ib - IVb, VIIa, VIIIa) not only form with Ti various pom-
ounds, but also can form solutions in it; finally 9 eltments
Zr, Hf, V, Nb, Ta, Cr, Mo, W and U) form with Ti a cohtinuous se-
f
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S/598/62/000/007/001/040
Metal chemistry of D267/D307
of solid solutions. The solubility of elements in Ti decreasesi
as the difference between the chemical-properties of Ti and the
element in question increases. There are 4 fundamental types of
phase diagrams of binary Ti systems. The problem of phase equili-
bria in these systems cannot be solved unless chemical reactions
between the elements in solid sulutions are allowed for. From the
behavior of Ti in binary systems it is possible to obtain the
general features of its behavior in ternary and mote complex sys-
tems. As regards the properties of mechanical stretgth.and heat
resistance, various binary, ternary~and more complex alloys are
adduced and described. The tasks to be given attention in the next
future relate to the further improvement of the quality of Ti used,
as initial product for high-grade alloys and the improvement of
the technology and investigation of new high-strength Ti alloys..
In this connection it is indispensable to reduce the content of 09
N and H below -.ertain limits, and this cannot be attained without
refining the metal. It is important to conduct further studies of
new alloys based on the so-called intermetallic solid solutions,
and of the Ti-Al, Ti-Sn and some ternary systems. Various fields
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8/598/62/000/007/001/040
Metal chemistry of D267/D307
of application of titanium and its alloys.are described. There are
14 figures and 6 tables. The most important English-language re-
ferences read as follows: M. Hansen, 'Constitution of binary al-
loys', McGraw Hill, New York, 1958; J. H. Westbrook (ed .Y, 'Mecha-
nical properties of izitermetallic compounds', John Wiley and Sons,
New York, 1960.
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S'A5P 62/000/007/0111/040
D244 D307
AUTHORS: Kornilov, 1. layeva~ Ye. N. and Volkova, Di. A.
TITLE; Properties of the alloys of the ternary titanium-alumi-
num-vanadium system
SOURCE: Akademiya nauk SSSR. Institut metallurgii. Titan i yego
splavy. no. 7, Moscow, 1962. Metallokhimiya i novyye
splavy, 89-94
TEXT: The work is a continuation of previous investigations of
Ti-Al and Ti-Al-Fe alloys. In this investigation the heat stabili-
ty of Ti rich alloys of ternary system Ti-Al-V was investigated.
Microstructure of the allo a at 6000C included either one o(-phase
or two phases cx, and (