SCIENTIFIC ABSTRACT YURGENSON, A. A. - YURGENSON, M. P.

• Document Type: CREST
• Collection: Scientific Abstracts
• Document Number (FOIA) /ESDN (CREST): CIA-RDP86-00513R001963210009-0
• Release Decision: RIF
• Original Classification: S
• Document Page Count: 100
• Document Creation Date: November 2, 2016
• Document Release Date: September 19, 2001
• Sequence Number: 9
• Publication Date: December 31, 1967
• Content Type: SCIENTIFIC ABSTRACT


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Yurk-ensou A.A., :,,engineer, and Pogrebetskaya, a' M
~ng ai~eer, 129 -8/17'
TITLE On reducing the brittleness of the nitrided layer of
the steel 38XMIA. (0 ponizhenii khrupkosti azotirbv-
annogo sloya stali 38K=uA,):
F&RIMICAL: "Ifetal love denie i Obrabotka Metallovil (Metallurgy and Metal
Treatment) 1957, No. 4, pp. 41 - 44 (U.S.S.R.)
ABSTRACT: The preliminary heat treatment. inf luences to a consid-
erable extent the brittle strength of nitrided steel. On
the basis of experiments, which are described la Some
detail, the authors recommend hardening from 930 C in
water since they found that such treatment ensures better
mechanical properti -es than hardening in oil, them, brittle-
.ness of the nitrided layer is reduced and considerable
A
savings are made in the quantity of required oil. A
sharp decrease of the brittle strength of nitrided layers
of specimens hardened from temperatures abovp 1 000 G is
attributed to growth of the steel grain and :~!onnation of
a nitride lattice. The investigations related ,;o cy-lin-
der liners, the material of which contained 0-39% Co
1.45yo Crt 0.6V,~ Al and 0.14yo Mo. 25 x 30 mm specimens
Card 1/2

On reducing the brittleness o .f-the-nitrided la ar -Q;f the
steel 38XWA.*(Cont.) 12F-4-8/17
cut out from annItaled tabes were hardened from g50, 9001
I 000-and I 050~wC in water and tempered at 640 0. The
holding time during hardening was 1.5 hours, duci-ng
tampering 3 hours.
There are five figures including two graphs, and three
Slavic references.
ASSOCIATION: Sverdlov Turbine Works. (Sverdlovskiy Tarbomotoxnyy
Zavod)
AVAIIABIB
Card 2/2

AUTHOR; Vyshkovskiy, YU*G. and Yurgenson, A.A*j Engineers.
TITLE: Influence of cold treaiment on certain mechanical proper-
ties of high alloy, case-hardened steels. (VIiyaniye
obrabotki kholodom na nekotoryyemekhanicheski-,Ye svoystva
vysokolegirovannyk1t tsementovannykh staley)
PERIODICAL: "Metallovedeniye i Obrabotla Metallov" (Metallur
and Metal Trea",-,ment), .3957, No-10s Pp. 37-35 (U.F.S.R-)
A. 2
ABSTRACT: Introduction into industry of cold treatment for elimin-
ating the residual austenite in the cemented la-yer of the high
alloy steels)BXBBA, 18XM-and lZK2H4A involves considerable
difficulties, as was mentioned in several publialn d papers
(2) to (5). Some authors pointed out that cold treatment
aff"ects adversely the mechanical properties-of cemented speci-
mens, i.e. not only the ductility but also the strength
values and Sadovskiy, V.D. et~alil (7) attributed this adverse
'effect to the formaVion of micro-cracks and Sokolovj K.N. (9)
recomaends using cold treatment only for comporants vhich are
not very highly stressed. The authors of this paper consider
it of interest to compare the influence of cold treatment on
the mechanical properties of the specimens for various distri-
butions of the residual austenite in the cemew .;ed layer. For
Card 1/3 this purpose, they Eubjected 30 ground specimeas, lOxlOxl20 mm

129 !0-,8/12
Influence of cold treatment on certain mechanical properties
of high alloy, case-hardened steels. (Gont.)
of the steel 181CHBA. to cementation at 890 0 fGr 9 1LOUrSS Using
a solid carburisation agent, whereby a cementation depth of
0.80 mm was obtained.. After the cementation process, one batch
of the specimens was cooled in oili whilst the other was cooled
in air inside the case-.hardening box- After cemextation, all
---the---specimens-we-m-coolcid-to=?;~---v Zd hold at that temperature.
3~hourel and,folloNving thatt 4--at-15070 -for-
or ;fiiY Ikere empeie
f
2 hours. Sojae of the -specimens.weire then'tested directly for
static bending whilst others were - tested for stati a bond ng
after grinding off 0.03 and 0.10-mmat-2 opposite edges in
the latter case, the grounds edges were perpendicular. to the
direction of the bending load* The...results 'are entered in
Tables 1 and 2. An increase in the:cooling speed after case-
hardening, which prevents the formation of troostite.-.6 'kin in
that part of the case--hardened layerwhich cointains free car-
bides, brings about an improvement in the mechanical properties
of low temperature treated specimens'as compared with those
which were cooled slowly and where conditions f or~ f ormation of
a troostite,edge are Mare favourable'. Removal of a part of the
Card 2/3 oase-hardened layer by grinding improves themechanical

1,?9-10-8/12
Influence of cold treatment on certain mechanical properties
of high alloy, case-haxdened steels. (Cont.)
propeities of all the specimens and the improvement is more
pronounced in the slowly-cooled specimens; *after grinding off
0.1 mm, the mechanical properties of both.groups.of specimens,
were almost equal.
There are 2 tables, 3 firguzes and-13 Slavic references.
AVAIUBIZ: Library of Cox%ress
~Card 3/3

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Y-MySu MUM
1.-N., doktor takhnicheskikh ne uk, pWesson, GITUISON, IU.K..
inzhener; FOOXEMSKAYA, T.M., inzbener; WaSON A.A,, inzhener.
Investigating the cavitation and erosion resistance of the 38KhMIUA
zinc coated 9-nd nitrid.eKI steel.. Voot.mash. 37 no.9,24-26 S 157.
(MLRA 10:9)
(Steel-Testing)-

SOV/137-59-3-7003
T ran a lation fronv Referativnyy zhurnal. Mletallurgiya, 1959, Nr 3, p 296 (USSR)
AUTHORS, Vyshkovskiy, Yu. G Yurgenson, A A.
TITLE-, -A Novel T echn9logic al Process of Ileat Treatment of Atomizer Hous-
ings (Novyy tekhnologicheskiy protsess termicheskoY obrabotki kor-
pusov raspyliteley)
PERIODICAL: Tr. Ural'skogo politekhn. in-ta, 1958, Nr 68, pp 132-140
A.BSTRAcC-T.- HeatAreatr6ent 11--atbinizer-housings --made -of-,steel. KIINVA114-
.d
-Pac
he- fol- bwing-p~rocee tires-
carrie ou in-accor ance -with
CI -burized I Iv-.ca.
burizing at4-teraperature of 880-9006C- until -a car ayer
0.5-0.8 mm. deep had been obtained (exposure time -3.5-4 hrs); cool
ing in air in closed boxes to a temperature of 700 or lower. Compo-
nents which had successfully passed metallographic inspection are
removed and placed into a cooler unit (direct contact with dry ice)
for a period of 2 hours; after drying at 1000, they are wiped dry and
are then subjected to -ndividuaL hardness testing (RA=82). This is
followed by tempering in an oil bath at a temperature of Z20-2400 for
a period of-5 hours - After tempering, 5-10% of-the components are
Card 1/2 again subjected zo hardness testing (RA=79-81), and the entire batch

- ----------- --- -------
iSOV/137-59-3- 7003
-Technological-Procest, of Heat Treatment of Atomizer Hoti.-ings
A Novel.
is then -tran s'fer red to the machine shop for final machining- The new heat-
treatment technology proved to be stable and reliable tinder Shop conditions. The
degree of deformation was reduced, better fits between the atomizer housing and
the needle valve were att-ained, and the- occurrence of rejects due to jammed
needle VZLlVeS was eliminated.
A. B.
Card 2/2

o'
SOV/226-7-.1-15/28
AUTH
AUTHOR:, Yurgens ------ ____
TITLE: Role of Hydrogen, in Nitriding of Steel-,(Roll 'vodorada
pri azotirovanii stall)
FERIODIGAL; Fizika Metallov i Metallove.deniye, 1959, Vol.7, Nr.1,
110-115 (USSR):
ABSTRACT: The influence of hydrogen on,the nitriding process and the
properties of the nitrided layer may be 9zerted In the
following direction: (1) As the quantity of hydrogen in
the gaseous phase Inareases,the latter occupies a larger
number of active centres on the-nitrided surface, renders
absorption of nitrogen more difficult and thereby slows
down the nitriding process (Refol). (2) An increase in
the concentration of hydrogen in the gaseous phase makes
the reversible reaction-of nitride formation go to the left:
lime mIqH3 !MGnNm -f- 3mH
Hence.- a surplus. of. atomia hydrogen in the gaseous medium
leads, to denitriding of the steel by lowering the surface
condentration of nitrogen (Ref;2)o By removing hydrogen
Card .1/6 from the- gaseous phase, it is ossible to accelerate the

~OV/126-7-1-15/28
Role, of Hydrogen in NitridinG of Steel
nitriding processe By placing FeSi into the nitriding
furnace, it is possible to obtain SiH&, to attain a decrease
in the amount of hydrogen in~the gaseoiis phase and to increase
the rate of nitriding (Ref.3). (3) At the nitriding
temperatures., hydrogen-is bound to cause decarburisatioa of
.-the me-tal- surface by forming hydrocarbons and destroying
-carbides (Ref*2).
MenGm -pH n9e GmH
p
ThisIreaction causes art increase in the brittleness and a
decrease in the surface hardness of the nitrided layer.
(4)_Kydrogen., having a small atomic radius, diffusei
easily into the metal0thereby causing decrease in plastic
properties and increase in brittleness of the~nitrided
layer (Refs.2p 4). -As the degree of dissociation of I
onia and the quantity of hydrogen in'the gaseous phase
amm
increasos, its action must increase. The Impact resistanae
and hydrogen:eontent after nitriding.metals with different
Card- 2/f; coatings, are shown in Table 1. From this il, can be seen

Role of Hydrogen in Nitriding of Steel
,that whereas-a t in~ and eopper.,c.oating fully protects-the
metal from being- saturated with nitrogenj hydrogen diffuses
into the steel through any coating, but most readily if
the-steel is phasphated. -- An additional tempe.ring at
~100-2000a brikigs about an increase In impact resistance of
nitrided spa6imens-P which is due to the influance of hydrogen
contained in the nitrided steel. - In order to study the
..decarburising action of hydrogen in nitriding, experiments
were carried out in which the change in carbon content in
chips was studied during prolonged nitriding. Also,
experiments were carried out in which the composition of the
carbonitride phases and the distribution of carbon along-
the depth of the h1trided layer was studied. Chips of
various types.of e~teel and east Iron were placed into brass
net bags., and nitridedunder production conditions together
with block cases in PNA-1 furnacesp bys, (a) heating to
510 �- 600 and holding at this:temperature,f'or 12 hours;
the degree of dissociation of ammonia does not exceed 35%-
(b) heating to. 540 500 and holding at this temperature
Card 3/6, for 38-45 hours: the degree of dissociation of ammonia does

Role of Hydrogen in N itriding of Steel
not exceed 66%; -(a) cooling in dissociated timmonis. (from
the adjoining chamber) to 20000. Simultaneously, 10 bags
containing chips.of one type of steel were placed into the
furnace. After the nitriding cycle was finished, all bags
were removed. Some of them were sent for chemical analysis,
the rest were nitrided again. ' In this manner the 6arbon
content in the chips submitted to nitridingfcr I - 10 cycles
was determined. The reaults oil this series of experiments
areshown In Table 2. From this it can be seen that as the
duration of nitriding increases the quantity of carbon Lyx the
chips sharply decreases, which is due to thedecarburlsitL4
action of hyd Irogon. 'For'a further confirmation of,-these re-
suits.the following experiments were carried out:- a strip
of the steel 65G, 0.15 mm thick., was nitridedfcw 1 - 8
cycles; half of-the specimens were nitrIded in the usual
manner, and half in bags filled with carbon. Data of carbon
Content after such,treatment are shownlin Table 3, from which
it follows that aitriding -in- carbon -brings._a:Oout_ considerabl7
For the-
ess dedarburisati6n than by-the usual method.
Gard 4/6 separation of carbonitride phases a method was used which

Role of Hydrogen in Nitriding of Steel.
Was suggested,for the determination.of the carbide.phase
in carbon steel (Ref.6).~ The change in carbon. content
6f the carbide-phase can be seen in Table 4. . Specimens of
steel U8., 16 mm diameter and 22 mm long, were nitrided in
the above manner for 1. 2 and 3 cycles, after whioli their
earbon-contents were determined. 'The results are shown in
Figs.1, 2 and 3, An investigation of the interaction between
I~yd.rogen in the gaileous phase and carbon of the steel has
shown-that in nitriding one of gaseous-compounds'
~is.prussic acid. From the above expatiments the author has
arrived at the fol.7' Lowing conclusions:
1. During nitriding, the carbon in the surfaoe of, the steel
,reacts with 6 gaseous phase, forming gaseous oompounds
(eyanides and probably carbon compounds).
.2o A decrease in carbon content in the surface layer lowers
.the surfaae hardness of the nitrided layerp and increases
the brittleness.
3. One of the reasDns for the displacement of the maximum
hardness into thedepth of the nitrided layer is the decrease
Card 5/6 in carbon content in the surface layer.

MFIRIV I, I

87947
s/iA/6o/ooo/oo6/oo6/oo8
E193/E383
AOTITORSi Kostenkol A*V*#-,Pogrebetsk&yaj T.M., Engineers
and- XSj&xensont A.A., Docent
TITLE: ~Study of Nitrided Steels I 5YjjPJ4?_ jl5KhllMF) and
(Sxac-tm(b (15Khl2VMF) After Prolonged Hol,ding
at 570 C
PERIODIC AL: Energomashiriostroy,eniye, 196o, No. 6,
pp. 33 - 36
-,.TE.XT: Owing to the necessity of using nitrided heat-
resistal2t- steels in turbl nes operating under conditions of
,high steam pressures and temperatures,,need has arisen to
determine the effect of t.-"Lme and temper Iature on the properties
of the-nitrided layers; hence the investigation described in
the present paper. The composition (in wt.%) of the steels
used in the experiments wits as follows:
steel l5KhllMF 0.15% C, 0-50% Si, 0.32% Mn, 10.62% Cr,
0.25% Ni. 0.70% Mo, 0-35%~V, 0.015% S and 0.02% P;
steel: l5Khl2VMF - 0. 13% C t 0. 26% s i. o. 66% Din, 12. 0~6 :Cr.
o.45% Ni, 0-80136 W, 0.59% :Ro, 0.20% V, 0.012% S and 0.02% F.
Car.

89947
s/ji4/6o/ooo/oo6/oo6/ooE;
E193/E383
Study of Nitrided'Steels 1!5KhllMF and 15Khl2VMF After
Prolonged Holding at 570 OC
The experimental test pi -eclas were heat-treated (air-hardening
from 1 050 0C plus tempering at 740 OC in the case of steel
15KhllMF and'oil-quenching~from 1 000 0C plus tempering at
700 OC in the case,of steel 15Khl2VMF), machined to
.10-x 10 x 30 'mm in size, electrolytically degreased, pickled,
phosphated and,then subjected to the nitriding treatment,
whichIconsisted.of 20 houris at 530 OC, followed by 20 hours
at .580 C, the degree of _dllssociat.ion of ammonia beins 35%
at the lower and-,651a at, the higher temperature._ The Rockwell
hardness of the surface of the nitrided specimens was
tile same'Lor both steels and amounted to 91 HRN; the nitrided
of.steel 15KhIIMF was slightly-thicker(O 37 mm)- than
that of the steel 15Khl2VMIP (0.52 mm). The nit~ided test
pieces were then held at 5*,?o 0C for 6 000 hours and during
this period the microhardness across the nitrided layer and
its thickness were:measured at regular intervals, and the

87947
.,;/JLl4/6o/ooo/oo6/oo6/oo8
E;193/E383
Study of 1q.itrided steels l5BJIllW and 15Khl2VMF'After
Pro-longed.Hol.ding at 570 'C~
microstructure of the nitrided layers was examined. 'Some
of the typical results are-reproduced-in Fig. -11 where the
2
hardness (kg/mm )-.is plotted against the distance (mm),from
the surface of the' nitride&layer on steels 15KhIIMF (graph a)
and 15Khl:ZVMF.(graph b); eXperimental points marked by, dots,
crosses,and circles relate to measurements 0 taken -immediately
after nitiriding, after 3 50o hours at 570 C, and after
0
5 000 hours at 570 C, respectively. Another set of results
,is given in Table 3:

8 4
s/i14/60/000/00 0"7"
6/oZ oo8
_EJL93/E383
Study of Nfitrided Steels l5KhllMF and 15Khl2VMF After
0
Pr,'olonged Holding at 570 C
'Depth (mm) r (determined by
o" the nitrided laye
Time Ibrs I- _-_ -I-- -
at:'570 OC microhardness measurements) on steel
l5KhllMF l5Khl2VMF
0 0.37 ~0. 37
250 0.50 0.45
15.00 0055. 0.50
0.55 000
~5000 o.6o o.6o
Meta llographica I examination of the test pieces showed that
the nitrided layer consisted of two (main and intermediate)
sub-layers, the intermediate sub-layer in steel 15KhIIMF
being more.sharply defined than that in the other steel. The
Card-ktlb

87947
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JP193/E383
Study of Nitrided:Steels 15Khllw and l5Khl2VMF After
Prolonged,Holding~at.570 o.,C
increase in the thickness of the nitrided layer after
holding,'at 570 *C,Was caused mainly by an increase in the
thickness of the intermediate.sub-layer, this increaso being
smaller-in steel :L5Khl2VMF. After holding at 570 0C, a
light-grey film wits formed on the -,surface ofspecimena of
both steels. X-ray diffraction analysis showed.tha,t 'the
n-
_M C 4_ A calel- consisting.- of. Fe--O Fe
'o stituted d
PeO.Zr - -6f:- t f
0, -the-two ~-stee- a- -a u ther va ~9~.-o -.--scj%
2 3
formation was'faster on steel 15KhIIMF.- After prolonged
holding~at 570'0C nitridee'i were precipitated at the grain
boundaries and the uppero nitrogen-rich part of the
Pt ta lator stage, these nitride~precipitates
became surrounded by an oxide layer. This effect in
illustrated in Fig. It, showing microphotographs (X540) of
the nitrided layer. in steel 15KhIIMF after: a) 256;
b) 3 000 and 'c) .16 000 hours at 570 OC. According to the
Ca-rd--5./W

87947
:s/114/6o/ooo/oo6/oo6/oo8
E193/E383
of-Nitrided-Ste.ele 'L3KhIIMF and l5Khl2VMF- Af ter
Prolonged Holding at 570 C
present authors, the, preferential oxidation of the nitrided
layers along the grain boundaries is associated with.the
precipitation of nitrides,which form a nitride-metal cell,
''thus creating conditions tavourable :Cor oxidation.- Andlysis
of the:results obtained led the prese~~t authors to ttle
:foll owi, ng co hclusiona
I-) A 414trided - layer foemed- on the:,mcre -- hest-resistant
steelA-5Khl2VMFI,is moreistable-at higher temperaturfso than
that . formed on steel.1501IMP. The former steel can be
recommonded.as the material for nitrided components operating
at C.,
570,."
Iml-order to-increase:,.the re-
-2) six _~~ce of-nitrided layers
agaInst -oxidaii= !dUr3*.ng--I~Gfir*idd--'AL,~?,-~ialievatiid temperatures,
__the~fi trILAin-g ~ -_ i,
Id -carZ
i d' L ch:.A manner.,
-procesA:- shou -Ibex.,. 7 :out- n.:su
asi to jpr vent the o mat .'on o -a h.-Itride network,
f
r 1;

879 7
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E193/13383
tudy of Nit-ided Stedl: 15KhIIDIF and 15Khl2VNfF After
s
Prolo
nged. Holding
at

e result:of
Th
w6rk:conducted at.the Turbomotor;txyy zavod
(Turbomotor Plant) has shown that the optimum properties of
the rUtrided 'layer
ckness of the layer 0.2
(thi 0. t* mm,
hardness not loss than.89 HIM) formed on high chromium-
~eont~nt steals-are obtained if the nitriding process consists

of :12 hours at 530 0
C' followed by'18 hours at 580 'C, the
degrefe.of dissocia tion:of ammonia being 35%-at the lower and
65% a,t the higher temperature. There are 6 figures, 3 tables
Soviet refer
-Ind ci ence.9,
,
Ox

8024
29/60/000/07/010/013
9193/E235
0
AUrHIORB: Qgte&)~g A. V, I~gpukhina, Ye. V., Foxrebetsk22a. T. M.7
and. X=ensorL",_jk. Engineers
TITLE: Structure, of ITitr-ideTtteel_j2Pj11W- After !Prolonged
Service at Elevated Teaperatures
_~__.J~9RIODIOAL: Metallovedeniy6 i termicheakaya.obrabotka metallov
PP.
TLTT: . Following theit earlier -f indiings-( e __ 1, -to---3)--that hardness-,--
of.nitrided gtainlesz and,austenitit steels 44cre.ased aftLer prolonged
~service. at high temperaturles, -Une presenT-a - ors. carried out a
s"Irstematic study of this effect on nitrided specimens of steel
l,)KhllVIF which is-frequently used as the material of some parts of
steam turbines, operating at approximately 5700C. The test pieces,
.,normalised at .105000, and tempered at 7400G. were electrolytically
dt~greasjed Pickledl ghosphated and then nitrided by a two-stage
Proces13 (k h at 530 C followed by 20 h at 50000, the degree of
dissociation of ammonia.being 35 and 65% respectively) which pro-
duced a nitrided layer 0.37 mm thick., with hardness Or, equal 95.
The structure of the nit3!ided lay-er and the effect of prolonged
Card 1/3

81824
8/129/60/000/D7/010/013
E193/2235
Structure of Nitrided Steel l5KhllMF After Prolonged Service at
Elevated Temperatures
(Up.to 5000 h)--treatlent a"~ 57000,in a was studied by X-ray
analysis, metallogr Iaphic-examinati6n, laicrohardneEIS measurements.
It vras established, that, starting from its -surface, tile following
strata. can be distinguished in the surface layer of a nitrided
steel: (1) Feg Fe4N + OrN;. .(2)~ Fe4H t a + CrN; (3) a + CrN;
(4) cc.+.carbides On heating in a*:~ an oxide scale "s formed
whose thickness, after 5000 h at 5~65c, reaches -0.0g.rm, and the
surface.jayer of -the nitrided steel after such treatment.-con~ains
the following strata: (a) Fe2O (m*crohardness - 768 kg/mm~'-);
71
.(b) F60h. (microLiardness - 455 k9/mm4); (c) PeO.Cr20-3 (microhard-
hess -'4 5 k&&W-); (d) a'. + CrIT + FeO,Cr 0 (e) cc :f Cr2N;
(f ot +: carbides. The most intensive -oxigNion takes place in the
-region which originally consisted of iron nitrides. This is att~ri-
buted by the-present authors to the fact-that nitrides*&Iform solid
solutions which are homogeneous within a wide composlulon limit and
which are characterised bir a high concentration of vacant lattice
Card 2/3

S/129/60/000/()7/010/013
E193/E235
Stru Ictuxe of Nitrided Steel 15WlMP,after Prolonged'Service at
-Uevated Temperaturea
sites J*'acilitating diffusion of oxygen. Since hardness of the
nitrided layer would be only slightly decreased by removing its
outermost part (,to a depth;'of say 0 1 mm), consisting mainly of
iron. nitrides such a treatment should increase the re sistance of
nitrided steei to scale formation on prolonged heating and so
prevent the decrease in hardness, usually taking place uader these
conditions. There are 3 figures, 2 tables and 7 Soviet references.
C aiA 3/3

5/129/00/000/011/004/016
80,7314J39
AMMONS i ql"kseo~ W lb.t.nkc, A. .. Rikh
V-x'0b-t*JCsy&. T-R- and rarx-e.a.A.A.,
TIM I Zorlsat,94 Or goat Treatment and Ifitrldt"
r on %be
Weakasleal Properties tf Anste"ITI-o-StFeel.
MILIOCUALs I tsrutch.wUsya obrabvtkm
TIMTs A "Arttot layer or mutealtle steel can be fert-
mogmette. although, too vor,% of the component can remain
DY thangL" *be VrallulahrY beat treatment it I* possible to obtain
as sastvalto with varlaus, docrees, of allarLet and varitue
04tvesuiefts, or tb* secondary rhsoev. Cb..Xsa 1,m the rb~.
Composition of -ustemttlc steel
- Y -b V1 - -- Iii
Ise r WS a W6 E-a VIA Its maxnetin properties d.. to rm4tI.A
of -r:mlte remittal from quenchlzg at elevated For
.,: ssou6 the authars considered It or.intortat to stndy the
lArlsouce, of prollaisary boat treatment and nItrLdIaX On th~v
of auet.nitic steel. Two stool. or the
Ift.42t,got.al (in
~St"l Vr: TI .5 3'
&.I )to Yi
D 14 W W=1/1 0.1t2_2? 0.63 I'k.$%.l3.R0 1.79 0.841 0.007 0.016
Co.33 17.78 8.70 0.64 0.013 0.020
Th* "Comitic were s%udI:td,:",er prvLLmi4ar:F best treat-
meat followed by ultrtUnS. Th. I ]Khl8N9T wax edU%1~11Y
subjected to -vrmg- alLrldtngk tinned p.41avus v*ro ha~2.4 itb
'A Wimultmeemaly with the rAtrld*d speti"ous or 104* San*
stool. The macastle, Properties *C the stool U2123 were determined
~&ftgr uOrSaUu&tISm annealing or art*r normalization annealing and
exetaX.- im. "- 1150 and 1C-WC~ The
yee"ALteary best treatment of the Stool llhl$?19T consisted In
"Omah&ng from 1~50*e to water and subw#qwont ageing. ftt?A stools
Calla
"Irs &Sea for a bee" *% 8001C. The specimen* were IS the tam or
2 See djametax,. 5 we 1*'L% cYllWd4'f2- The "Ag"Atle Susceptibility
r the stool* xtli5 mad xiblasgr to the ps,r*-axnatte state -a
e
NoseerSd by Seems *frUcZU't'o ot"'S at "arlo"a field
an to determine the 'X(M). ftr Lnvev%1Xe*iug C-16 ~JQ;
t the aLtrid*4 Nt**16, specimens Ln the form of.tubso wtltb am V
:sterux diametcr Or 4-ma. a loft3th of 60 oft and & well tJaItJ=.%S of-L,
0.5 Se' "s'S, surfac"of the opecLaass wors, gro"d
Lnt:%.L Th* S."r"I
machined by man. of a reomor.
*"l:tttb* triding. tuo none wwro.otch*4 in a hydrochloric &6l4
Pris, a =I
--salution at 70*C for 5 ain ."d then nltriddd~lft a laboratorY V,"*46
at 600*C. with'- hwl&isg tie. or 65 homr. for the steel 9nZ3 and
73 to 95 hours ror tb, steel lKhlBTt9T. The 75 hour holding time
oarresponded 10 the immLoun depth of the aLtridtd layer for spotless.
vItb a vall thicksoc* or ().5 me. lh~ magnetic properties of ultrldtd
specimens were a.-- cArco&t.
0m the bodto of the obtained results, which are given. the following.,
eaftelarione "a arriewd at z
card 3/5

in 11111 3 5 2
A.-V4,,, Lopukh a
AUTHOR5 JCostenko. etskava, T H.
and Yurgenson., A.Aa
-TITLE:
PeculJarities in the-Behavlour of-Nitrided Type lKhl8N9T
Steel During- Prolonged Residence at a HigJi Temperature
PERIODICAL: Fizika metallov i metallovedeniye, 1960, Vol 9, Nr 6,
877, (USSR)
pp
ABSTRACT: The authors point out that the nitridinp, of austenitic
steels. has no'L been used in gas _.turbine7-R;onstr ,uction
(Ref 2) becau;se of process and -:f iniiiiiai:'difficulties
_.an& -the- insufficient. high-t amp er,&t.ur_O_ -at ab il:L ty.1, of the
-nitrided layer (Refs 3,4) A previous study by the authors
of a group-of nitrided steels (Ref 5) showed the superiority
of type IKhl8.NgT steel in these respects and the present
investigation aimed at a more detailed study. Specimens
1 (0.10.
of the stee C. 17 -a 809'3' Cr, 9-7~6. Ni, o. 645.1 Ti,
0.0121,04 S1 0.020% P, 0~531,11o Ila, 0.581,,,.' S:L) ifere hardened
OC_: 0
from 1 150 aged,for, hours at 800 C, pickled in
hydrochloric 'acid and nitrided at 6oo 0C for 75 hours.
--A -0~29__Mm__ deep-nitrided, layer -with-14- hardness
H
--R--- -.92
Cardl/4 N
'was obtained.. The kinetics of v eact ion-4i f fus ion . of

80885
S/126/6o/oo9/o6/(II.d/o25
Peculiarities- in the. Behaviour. of RRIMPTYpe lnU8N9T Steel
During Prolonged Residence at a High Temperature
nitrogen and c n t e nitri.ded,layor during
-hanges i
-prol -holding at 680-C.-in.1urnaces- (if a.-type IP-2
onged
Machine (as described in Ref 6) idere invostigated. For
studying phases at.increasing depth beloy the surface
of the nitrided and sca."Le.-layer X-ray _structural analyses
of successivejayera: were carried -out at the-Ur-alfskiy-
-gosuniversitet_ (Ural--State- UnLy~riilty)._ :bi --consultation.
with V.N. Kon6v. Figure 1 shows.the striicture of the
.-nitrideg layer beforeandafter holding for 3 000 hours
at 68o, C, idzile the oxides on an -etthed polished section
after 250 hours, is, shown in Figure 2. The linear relations
between the square of the gain in w6ight~,(g/mm )(Curve 1).
and the -square of the-depth (mm) of the nitrided layer. on~
the one hand and the duration -of nitriding (hours) on the
other g3-ven in- Figure -3 __Jndicates_a~ parabolic law, for
nitrogen diffusion. The X-ray-patterns 0Xrom succesive
layers before.and after.holdIng at 680 c for, 4 500'hours
are shown In Figures 4 and 5, respeetively, the natur e,
Card.2/4

0885
s/196/6o/009/06/01
Peculiar�t�es in the Beha'viour of,N:itr,l e. lKhI8N9T Steel
~Durinj~; Prolonged Residence at a High Temperature
the -ph.as es b Oing listed in Tables I and :2t respectively.
-The, isurface hardness of~, the nitrided. steel is plotted.,
a Ig inst dura 14, ion.of holding'-(hours):at _680- ."'CAn Figure 6,
a
e ed~
the corr spoixding effect,on the depth of the-nitrid
layer being shown in Figure 7 (Ourvesll, -2 and.3 refer to
the-Vhole, bas-e-I -and transition layers, respectively).,
FigiLre 8 shows hardness as-a-function OX -depth below
surf ac e b efe re and after holding for - 5,4300 .hours,, (Curves 1
a .nd.2,- respoctively). The.work showed 'that-saturation
ofthe steel with nitrogen leads-to austenite deaomposition;
the -nit rog.ej: - -is fixed as ~ a nitride with the CrINVtructure*
Prolonged., liolding at -680-~-.- -C: gave -an., out-er scale layer of
r of (Cr,~F
f erric oxide and an inner layt. 020 iron
nitrides dissoclate;l instdo the ded,layer complete
nitr:L
austenite A,ecompositlon occurs 'with eqEWILzatIon of
nitrogen cc-noentration with depth and formatIon and
co,*Z. u-tat iori of nitrides. - The authors, recommend that
n1triding (.ond:Ltions_I:8hould'_:_b'e -5eleated to give the greatest,
Card3/4' -quality of stable nitrides (not iron, I initridea): mechanxcally
LI

,4T

5/129/61/060/012/002/005
1.11300 F,193/9383
AUTHOR: Yurgenson, A.A~.', Engineer
TITLE., Selections of nitriding schedules and depth of the
nitrided layer
PERIODICAL: Metalloved.laniye i termicheskaya.obrabc,tka metallov,
no. 12,-1961, L3-_ 16
TEXT: Side,effects of-nitriding are discussed in relation to
the mechanical propertles.and corroslon-resistance of nitrided
steels. It is pointed out that one of the consequences of the
formation of nitrides is~_the formation of interphase boundaries
witti a heavily-distorted crystal lattice and refinsinent of the
mosaio structure. Thus, in steel nit .rided.at 520 C blocks-
measuring 5 x I O~-5 CM app ear.,.as a result of which the surface
area of the sub-boundaries with-distorted crystal lattice
increases and internal sitresses of the second type and distortions
ofthe third type appear in the metal. -Internal stresses of the
first: type are set xgp as a result of different thermal-
expansion coefficients of the matrix-,and nitrides, At the same
Card l/ 7

S/129/61/000/012/602/605
Selectibns of nitriding E193/E383
time, the solid solution is denuded of the alloying elements;
as a rosult, the stability of the solid solution in austenitic
steels is. decreased and the car roslon-reststanc e of stainless,
acid- and oxidation-resistant steels is reduced. X-ray-diffraction
studies of the distribution of stresses of the first type has shown
that the maximum.cbmpressive stresses are situated all. a certain
distance from the surfaceu The magnitude of the compressive
stresses decreases with increasing content of-the c-phase in the
nltrldod layer; when the e-phase content exceeds 504,~ tensile
2 . j
stresses of up to 20 k9/mm are set up in the surface layer
(Ref '0 2 - Fuks, M.Ya. and,Tkach, A.Ya., Trudy KhPI im.) V.I.
Len.ina. Seriya inzhenerno-fizicheskaya, v. 14, 1958). To
attain maximum endurance limit, the formation of a siwface
n1tride film or ex nitride network must be avoided anti the depth
of the nitrided layer,.n., must meet the condition a /r = 0.1
002, where r is the distance botween the neutral axis of
the material and the most heavily-stre6sed fibre. In the case
of localized nitriding, tensile stresses which decrease the
Card 2/7

S/129/61/00 012/002/005-
Selections of nitriding E193/t383
resistance of the metal to cyclic loading are set up in the
surfacia layer at a certain-distance from the boundary between
nitridiBd--and-untreated parts; this boundary,
-theref-ore,should
not be:placed in a region whicn carries service loads. Nitrides
of Feg Mo and probably Mn readily oxidize, in airl if nitriding
conditions~are suchthat,~ the steel is supersaturated with
nitrogen, ox:Ldes-instead of n:Ltrides,,may beformed with a
Ah
corres'ponding change'in, ', e properties o- the nitrided layer.
An oxIde scale is readily formed on.nitrided steel at 550
0
68o C :in the presenqe'ol~ a nitride network (Ref. 8'-
A.V. Kostenko, Ye.V. Lop~tkhina,. T.M..Pogrobetsk.aya and.
A..Ao Vargenson, -. FMM., v.*11, no. 6,.196o). A 17-fold increase
iri'the resistance of steol. 38Y\VAVOI~ OfthWUA) ~to cavitation-
erosio'n--is attained.by nj;triding. It..has been shown., however
(Ref. 10 - V.V. Gavratselt, D.N. Bol'shutkin Trudy KhPX
Vo-1. Lenina.- v. IX,. no. 1, -1957) thatI.the erosion stability
JLM_. L/
the e-- and y'-pha -that of the
f. seji. is- 14 times lower-than
o
a"phase. Corierequently, -,,L,f -the-maximum resistance-to-cavitation-
erosion is to be impart ed* to a pearli tic st eel, -the formation
Card:3/7

j
611660/
Of2/002/005
;/9/33
sele^tions of -ziitr ng ,Z19 83:,.I~'111
of a suxfal~.e' 'layer with ~a- minimum content of--the c-and
phases-~should-be- -aimed, a!,- -in, nitriding 0 Maximum hardness of
yer is at! at- a- certain~-distance from the
the nitrided, la
iixereasing withincrea -dopth of.
surface,-.-th:Ls distance sing
nitriding. When thiS-object-of,nitridlng is to improve the
corrossion-re5istance of :6teel, a,continuous,I-surface, -film of the
~c-phaswahould be formed. ..The quantity of the e-phase can be
increased b 'raisi g tht'nitriding temperature to 700 OC. All
y. . n 11
the alloying'~ additions, Oxc~ept Al decreasethe depth at which
nitrol .;e n-ricb phases arot for med. The quantity of the c-phase
formed depends also-on-11-he relative rates o7f adsorption and
diffusion of nitrogen..71f adsorption rate is higher than. rate of
diffitision,,-the -surface- J)ecomezzat.urated -with nitrogen and a
nitride'skinlor network,is. formed. The rate'of-nitrlding can
be increased by raising.the temperature which, I~pwcver, brings
about, a decrease in thd.surface hardness* For this-reason,
a two-stage proces -aprovides the most convenient nioans of
forming a nitride layer.more than 0.25 -7 0.30 mm thick in a
relalively~ short, time. Nitriding is carried out in the first staSe
Card. 4/7

5/129/6.1/000/OJL2/002/005
Selections of nitriding
at 504)1+-10 0c for 10-:15, hours t o' produe ea hard case.
The temperature-is then:raised to 51i0 - 580 C for a short
~time,,whereby the rate-cif diffusion of nitrogen-is increased
without significantly affecting the hardness of.the surface
3ayer, The properties of the nitrided,case can be affected
by the composition of the nitriding medium. Hydrogen formed
as a result of dissociation of ammonia retards the diffusion of
nitrogen, decarburizes the steel and decreaoce -its p1mattoity,
According to A.V. Smirnov and L.V. Beloruchev Uef.13- Controlled
atmospheres and their uve inthermal and ch'emitothbrmal,
treatment of metals, wimp, 196o), improved results are obtained
if a mixture of -ammonia :x-rith an inert gas - (molecular nitrogen
or hydrogen),is used insitead of pure ammonia. TBmBry.'T
"Kohfiszati llipok", v. 2, no.-5, 1956) has shown that
the rate of nitriding cim be increased by using pure (990,1))
nitro.6ren,instead,of ammonla.. Similarly, a harder case on a
manganese-cast iron waslobtained in a 65% nitrogen -55% ammonia
mixtu:.re than that formed in pure ammonia.(Ref. 15
Yu.G. Bobro, V.S. Koval(inko - Trudy KhP1 im. V.I. Lenina,
V. qj~no. 1, 1957). In'general,_a minimum thickness of the
Car& .5/7

S/129/61/000/012/002/005..
Selections oUnitriding 9193/9383-
nitrided caseshould be :aimed at, whereby the prod.uttivi,ty
the. nitriding --equipm eat incr eas-ed -and .-the-xisk--of .-warping.
and distortion of the nitrided particles is 'Minimized. Some
consideration should, be -,given - to - the geometry -of a nitrided layer.
The risk of distortion ip -less when the entire surface is
nitridled but, in this ca:6.0, the dimensional changos~ of the.
Whe only a~part of the surface is nitrided,
articl,.e are greater., U I
the nitrided catte should~ be symmetrical since, -otherwise,
distortion'of the articl;e,will take place. In the case of
stainless, acid-- and oxi.dation-resistant steels, those parts
of an article-should only be nitrided which carry alternating
servic.e loads. With the'exception of applications in which
nitrid.In g is- usedto increase, the corroslon-r6s1stance of. steelq
the optirmim n.1triding conditions are, tlhqse which ensure.
conversion of all the alloying elements to nitrides:and the
formation of a minimum quanttty of iron nitrides.
[Abstracter's note.- this is an abridged translation.1
Card 6/ 7

PHASH.I.BOOK.MLOITATION
YurgenSon, Aieksey Alekieyevic SM/W8
Azo.tii~-!:)irsLniyi~,.v..4,ndrgomas yenii Ib ~~
hinos-tro -(Nitriding '6wer-Plant
Ifte-11i Building
nel -Sverdlovs%--Mash iz, ~962. 128 p. - 2800
coples printed.
Re,vieye .-M. Lakhti bf--Tech
r* -YU n Professor,-~Doctor nical-.Sciences;
Teph. 'Ed. N* A* Dugina; lFixecutive Ed, Of Urql-Siblaiiian
DeDiirtnient (Mashg1:t) A Kaletina Engineer.
FMIP.0311: ..This book is intended for process engineers and mechanical
It may also be.useid~ to worker~d'of
do,:L."eratific rel3earch instit4tes 66d.laboratories.
COWUkAdE: *e- -book- describes the n1t. riding; methods-and c6ndftions,
which iwill improv6 the ; 4ua,lity of:the n1trided cases anV 'Is'
on'! of -practices -and ini
based vestAlts rdstigAtions: of plants'.
whaiah'haVe been using bhe- nitriding o. f Impokant-machine parts
Ovefj.,. iQng pe~rlods uf Iv- -1yao. Possibilities of applying'the nitrid-
_.)jj
ing!-Procesa,,to heat
otuller

00 Y-
S/11 2/000~fb'08/WS/005
207
AurrHORS 1, Mikhalitaina, Ye..G. p Revzinag V..G. 9and Yurgevson# AIo.A,#I----.
TITLEs Phosphate coating of austenitic steel
PERIODI(aLt lb.131.inostroitel', no-6v 1962t 35,
TSM- Results are reported of experimental investifationei. on-the
phosphate coating, of austonitic. r-teels, in ordor*t'O' improve) working conditions,
reduce rv a
ripping (saizing)- andlNear and increase the so ica lif of. phosphate-
coated tools. Special irdications on the phosphate-boatirig teckmologyo and
test regiults are presented. It was found that auetendic citsels may be success-
fully 1~~toaphate-coated by applying special preparatory methods (elect'rolytle.
degreazbkl~v-pickling) and by-utillsing special, sle~trolytvs. in cleatrical
solutionse The re is Itable.
Card III

705
S/126/62/013/004/019/022
E073/P,135-
4P.
AUTHORS: Belenkova, M.N., Mikheyev, M.N.,
Pogreibetskaya,, T.M., and Yurgenson, A.A.
TITLE. agnetic-properties of the steel 1 18 H 1) OqAhlft-9)
afte2- heat-treatment and nitriding
PERIODICAL: Fizilca metallov i metallovedeniye, v*13* no*4, 1962,
622-625
TEXT: The authors and their team found earlier that the
greatei- the content of elements forming stable nitrides, the more
v.,ill the austenite becomo impoverished of alloying elements
duringnitriding and the-moro intensive will-be its decomposition
and thf.3 rejection of the~:a_phase.- The influence of nitriding on
the ma'Snetic properties of steel similar to the previously tested
i x 18 H 9T (lKh_1%8N9T) steol but not containing titanium was
ztudieid to verify this conclusion. The compositionEl.of the two
-steels. studied were:
inluq: o.14,Z' c- o 6654 i5i; o.85% ma; 17.68% Cr; 9.02%.Ni,
0.07% 7-1; 0. 616% S; 0. 016% P.
Card 1/4,

S/126/62/013/004/019/022
Aa&netic properties of ttie steelea.
E:073/F,135
lKhl8NOT: 0.1% C; 0. 58% S 1 0 53%- Mn;, 17-78% Cr;8 7036 Ni;
o.64%, ri; oAn%j S; 0.02% PO
The.magnetle properties vrere determined after heat-treatment
(quenching from -1150 *C in water, followed by ageing for 8 hours
at 8oo~ 0C). Bot'll stoolL were paranjagnotic in the quonclied state
and their susceptibility values were noarly the same. After
againg the susceptibilit]r:increased somewhat, the permeability of
b~_;th- steels after quench'4ng~ and ageing.- approached unity and did
not depend-oxx the field i5trength. In the nitrided titate the
niax:Lmum permeability of -the steel without Ti was considerably
lower.than in the steel ifith.Ti. For a relative depth dfr the
the: steel 1Khl8N9 had a maxi.
nitrided layer of 57.4% mum
meability of 1.8 gauss,(Oe whilst for the steel lKhl3N9T the
er
p
-gau e
maximum permeability was 3.7 ss/Oe,for a relative d p:th of,
the n*;trided layer f 50%. - The structures of the nitrided
0
layers of both steels.were identical, consisting of austen1te
and carbide grains in the heat-treated state; the jitructure of
the nitrided layer was reminiscent of sorbite, due to the
partial decomposition of the (X-phase and the carbides during
Card 2:/4

S/126/62/013/004/019/022
Magnetip. properties of the! steel.*#
E073/E135
nitride-..formation. The following conclusions are arrived-at:
Nitriditig changes considerably.,the magnetic properties of7steels
-erromagnetic nature--of the nitrided
...lKh18N9i nd lKhl8N9T-, the;f
-p ng,,
..layer i4i due.. to the formation of the Ot hase during nitridi
-,The stee:l- lKhl8N9T has a higher permeability--in the nitrided
state than the steel 1Khl8N9, and the difference is attributed
to the presence of-Ti in the former, which forms stabLe nitrides
and impciverishes.considerably the y-phase of Ti, reducing.its
stability and- bringing about rejection of (X-phase. Tbe- stability
,of the Z,ustenitic structure after nitriding was determined,by the 14/
concentration of admixtures required for forming uniform
austeniteand by the ability of the components entering into the
austenite to form stabl .e matrides. The nitrided skin' of
austenij,;Iic steel.components should have low.permeability values.
There are 4 tables.
Card 3A

a

-, I

R: i) A
AN I
ACZEM 0 -N 0' AP5CC,14~4 S/0114/64/000/008/0032/0036
"-j n 7-3 i ru; Y-C (7,ni-Irtmer)., Rorgrelbetiskaya-, T.-M. Nngiineer.);
nit ridinz of -:ast turbir.,~, parts
J6,
n , n ida t i tj
&;,n2
f, t (ILTO g, t v11 Im I~he irle-i-r- -!Lion, st-ruc-
Alli PlIaze. nlaqm
7 agt i ront, SCb2l-
nc, 6ic 0~ rr 6~01,
gi!
all

AF'50
anew tilictile I ropertics -~mx (lie-
)5L !:_iecl by .,',,e "olloving mode:
--Olould )-.,IV(, a wirface `L*ais'-.
of cast j-mn,4 i;;
-nc, _-~e in ha'- "Was, Sat, r-,Iti,On Of CUst, iMn MAIZI-40 with nitro-
catt!" e '3 ca,3t steel imd irua pa.--,s ,3
Or; ae
ow,:-. r a t h
SUB cloDE: KM, FR
lu'R: JFRS
RE'f' iOV: 0,05

t; -nzj~ Lj
'r1
4_ T Aa,
f Ott I
9 t4! okho~ftykh-__: d 't 1 -0 Y_ I a'A- ~K ly, V M I p k a
royen
4'
ut;~r'~b Lb I i0fi! Ute
77-
-TAGS-V_ _A41is- _61 7-4ti-il
A
we mkdkia
-b~o ~o 61 -To Mac C
A ac affii C
a t
'31ft-r. ine"riz, and heat-trectment s pet La I is.ti: wo-rk fiig in diese'l engiive
5 S f -,I Or wn rk,!;r a -i t
:4 ii% cy L L t_i ',a& a.-. ;1. z 41 d c ait- ~n Ive a I t I z T 11 v L, n 0 k 1: 0 v
__rEtu~. T.C
7 f -ar diege
V thjk7~! it P_ d
4
jroq4 a P_
Ong klea Sives info rma tio'n on qualitiesi
all)yv uced for -a-an u f a a t u r n g high-speed 414ase-1 4ugln 1;0 di8CAXSdftS
s Ij a t c fa at -~:Ten a f beat kreatment, and akig faethods for in-
aretaling the 1ife of individual partt,* Subatitutc materials are
dia!uazed sud general raeomandAtLon# for 1 Ateffal selection are

Le e I for h tgh ti exised a rtq in cj iewh I a nginc a 19
till Rntar-Ijil for vIlrder it! eve.-
teptg f or valve S', 90
r p r e C.a V (4 rn
T T rn g
Card

L4~~- z
AH~
a h i n g D e a r 1 7
I m I r a 0 c g s n 1 )9
Refereleiao 248
S T
si t
S LTi'l 1: TT E I A Av r 6 NO REP ';OVt 2 so

_L 29833-6 M(M~ZEWWZVE_ _-UP(al JD.
-UR/022 T007WO076.
Rd N&7V6012239.
R lurgens IA A j 2:aVazdi na,, Y4~_V.
_MTHORS on
~,' ""IT
ORG.- Tarbine Nin3 Works (Turbomotornn zavod):'.
TITLE.- Maltiple nitridins lKh13, 'teel
-SOURCE: Ketallovddeniye i terutchaskaya, obrabotka metal4V,_.no- 4* 1966 75-78
TOPIC TAGSt chromium steel,, - nitridation, x ray photogra Iphy,-x ray equipment, ammonia,
phase composition/ IKW chroidum steel-, RKD x ray equipment
ABSUMT 3 , Specimens, ot_'Uh13 ,steel were nitrid, od in And~wteial furnaces under the
at 540P -for -12 * bra;
toll6wing canditfori~vl - heatin1l ammonia diadociation-to 35%j-.
heating- 0~t-.540C- fAr___48 _11rej- Mmoniadissooiation toL 6~%j __c*c61ing-_u'ndar ammonia.
atreameto- 2000; - air cooling.___ Thii.process was-repeated.- X-rV photographs were
taken with a RM-camerat -Iniwltiple,nitriding of high-chrome steel$ the surface
layers were decarbonizeds-'iri)n nitrides-reactedwith atmospheric oxygen and-formed,
-has a contains iron oxide
iron oxidest Chrome steel iftich -been nitrided nine time
and nitrides. on the surface; phases. containing chromim- are absent* Excessive and
repeaUd.nitriding Upairs th4-quality-of the nitrided I of high-c1mme steels
Ori A -has 1 2 figures' 1 2 tables
ge a 0 aw,
SM'Cost"- n/ SM:D&91:,~ none/-, -:.ORIG REFt, M3
'Gaid AA UDG t 621.78543 669.1h.018.25

~O ~ -',r on-Wteol.
t
p lop .q~ A"-b
,proftac e. tAtri ng.
Jf
-,qv:qpqqimen8~- d6a
ing-Ats 6 A
alne 0. 0 16 11 6~~ a- h- d
d1. 19% C; ~G. 2154' Si; 0 207o h1n; 0. lnq~ P~; 1,
'r W'.' Stage :-(1) 510 C for
0 niltriding wak; carried out in the -fo gypng, r,)rq as
mmoiiia'dids-ocialj (2),.54OC- fdr~ 48 hm,-----ar#znomJa dis;5ociat-lon
ge c~ulioriltridea wereIpd in,:an,-atniosp er -100
Z) p7 thd--initl2l: sta h e of
Wei tirl
C-O an 9,010 TIF Al.ter a Wnfold nitriding the 0. 98 mm tXfc-Ik d a-B--e consisted- of
Fe,)D-, oxide an4l,e nitri(.~as whereby tilie iron oxide had ar, Fe304 8tructure
f : -r
a A.W
o 1 2 am Q. mt gk4ing the nitriding

czi'sewits caused-.
)01

84286
Investigation of the Structure-of Turbulent S1050160100,61010IM11003
Motions Caubing~Bumps to Modern:Airplanes
,express the,relationship betweenithe dimensionless random values of
pulsation of the vari6us.kinematic parameters 61 the Plane and the
dimensionlegis functions TO i n- the form of equation (4). It time. The
Yk,
author makeg, use, Pf'the general- i3olution- obtained- in Ref :2 and obtains
formula The latte -r is integ:,-ated, and the..structural. charai;teristics
s s -of cr~.teria de-
of the ~Iturbulent flow are thoroughly,: studied. on' the ba i
-me eor- 1 conditions. Using formula (7) accordiag'to the
pending t' o og3.ca
2/3-law by Rholmogorov-Obukhov ' the author obtains formulas (8), (9), and
.(10). The-practical,application cif these formulas is illustrated by the
calculation'.of characteristics of the pulsation values of the components
of flying s:eed (
P and ~,)-as dependent on the meteor ological parameters
-(Akg 4,1r 0 Aetermining the respective turbulent medium. Ak is,a coefficient,
and A =1L
Ic The curves shown in Fig. 2 were obtained in the courise of
2
computationa"made on the electrouLb computer "Ural"..Theae curves illustrate
the dependence of fluctuations of-the horizontal (Fig. ~a) and vertical
Oig. 2b) cotiponents of:flylng 4p,Oed on-the intensity of action of horizon-
tal and ve rtical turbulent flows.iOn the basis of the rules resulting from
Card Z13

7
84286
Investigation of,.the Struczure:oi Turbulent -5/050/60/0,00/010/001/003
Motions CO,ualng Sumps to Modern Airplanes_- B0112/to63..
these-curves, the author-reach~Ds the,followirig:conclusions-. 1) The highest
probability that-a modern supe:rfast- airplane. with a speed,of 0.54H