Diffusion of Nitrogen and Phase—Structural Transformations in Titanium
The process of high-temperature nitridation (Т = 950°C) of titanium is investigated analytically and experimentally. The role of nitrogen as α-stabilizer in forming of nitride layer and diffusion zone, which contains three layers (layer of α-phase, layer of α+β-phase, and layer of β-phase), is shown...
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Інститут металофізики ім. Г.В. Курдюмова НАН України
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Tkachuk, O. Matychak, Ya. Pohrelyuk, I. Fedirko, V. 2016-10-10T19:13:26Z 2016-10-10T19:13:26Z 2014 Diffusion of Nitrogen and Phase—Structural Transformations in Titanium / O. Tkachuk, Ya. Matychak, I. Pohrelyuk, V. Fedirko // Металлофизика и новейшие технологии. — 2014. — Т. 36, № 8. — С. 1079-1089. — Бібліогр.: 6 назв. — англ. 1024-1809 PACS: 64.75.Nx, 66.30.Dn, 66.30.je, 68.35.Dv, 81.65.Lp DOI: http://dx.doi.org/10.15407/mfint.36.08.1079 https://nasplib.isofts.kiev.ua/handle/123456789/106996 The process of high-temperature nitridation (Т = 950°C) of titanium is investigated analytically and experimentally. The role of nitrogen as α-stabilizer in forming of nitride layer and diffusion zone, which contains three layers (layer of α-phase, layer of α+β-phase, and layer of β-phase), is shown. The approximate solution of formulated task is obtained for diffusion of nitrogen in such a heterogeneous medium, taking into account the motion of interfaces. The constants of parabolic growth of layers are calculated. It allows foreseeing the kinetics of their growth and distribution of nitrogen in diffusion zone. The microstructure evolution of diffusion zone (after processing times of 1 h and 5 h), which is caused by the phase—structural transformations during diffusion of nitrogen, is fixed experimentally. Процесс высокотемпературного азотирования (Т = 950°C) исследован аналитически и экспериментально. Отображена роль азота как α-стабилизатора в формировании нитридного слоя и трёхслойной диффузионной зоны (слой α-фазы, слой α+β-фазы и слой β-фазы). Получено приближенное решение сформулированной задачи относительно диффузии азота в такой неоднородной среде с учётом перемещения межфазных границ. Рассчитаны константы параболического роста слоёв, что дало возможность предвидеть кинетику их роста и распределение азота в диффузионной зоне. Экспериментально обнаружена микроструктурная эволюция диффузионной зоны (после времени обработки 1 и 5 часов), которая обусловлена фазово-структурными превращениями во время диффузии азота. Аналітично й експериментально досліджено процес високотемпературного азотування (Т = 950°C) титану. Відображено роль азоту як α-стабілізатора у формуванні нітридного шару та тришарової дифузійної зони (шар α-фази, шар α+β-фази і шар β-фази). Одержано наближений розв’язок сформульованої задачі щодо дифузії азоту в такому неоднорідному середовищі з урахуванням переміщень міжфазних меж. Розраховано константи параболічного росту шарів, що уможливило передбачити кінетику їх росту і розподіл азоту в дифузійній зоні. Експериментально зафіксовано еволюцію мікроструктури газонасиченого шару (після витримок у 1 і 5 годин), зумовлену структурно-фазовими перетвореннями під час дифузії азоту. en Інститут металофізики ім. Г.В. Курдюмова НАН України Металлофизика и новейшие технологии Дефекты кристаллической решётки Diffusion of Nitrogen and Phase—Structural Transformations in Titanium Диффузия азота и фазово–структурные превращения в титане Дифузія азоту і фазово–структурні перетворення в титані Article published earlier |
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Digital Library of Periodicals of National Academy of Sciences of Ukraine |
| collection |
DSpace DC |
| title |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium |
| spellingShingle |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium Tkachuk, O. Matychak, Ya. Pohrelyuk, I. Fedirko, V. Дефекты кристаллической решётки |
| title_short |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium |
| title_full |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium |
| title_fullStr |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium |
| title_full_unstemmed |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium |
| title_sort |
diffusion of nitrogen and phase—structural transformations in titanium |
| author |
Tkachuk, O. Matychak, Ya. Pohrelyuk, I. Fedirko, V. |
| author_facet |
Tkachuk, O. Matychak, Ya. Pohrelyuk, I. Fedirko, V. |
| topic |
Дефекты кристаллической решётки |
| topic_facet |
Дефекты кристаллической решётки |
| publishDate |
2014 |
| language |
English |
| container_title |
Металлофизика и новейшие технологии |
| publisher |
Інститут металофізики ім. Г.В. Курдюмова НАН України |
| format |
Article |
| title_alt |
Диффузия азота и фазово–структурные превращения в титане Дифузія азоту і фазово–структурні перетворення в титані |
| description |
The process of high-temperature nitridation (Т = 950°C) of titanium is investigated analytically and experimentally. The role of nitrogen as α-stabilizer in forming of nitride layer and diffusion zone, which contains three layers (layer of α-phase, layer of α+β-phase, and layer of β-phase), is shown. The approximate solution of formulated task is obtained for diffusion of nitrogen in such a heterogeneous medium, taking into account the motion of interfaces. The constants of parabolic growth of layers are calculated. It allows foreseeing the kinetics of their growth and distribution of nitrogen in diffusion zone. The microstructure evolution of diffusion zone (after processing times of 1 h and 5 h), which is caused by the phase—structural transformations during diffusion of nitrogen, is fixed experimentally.
Процесс высокотемпературного азотирования (Т = 950°C) исследован аналитически и экспериментально. Отображена роль азота как α-стабилизатора в формировании нитридного слоя и трёхслойной диффузионной зоны (слой α-фазы, слой α+β-фазы и слой β-фазы). Получено приближенное решение сформулированной задачи относительно диффузии азота в такой неоднородной среде с учётом перемещения межфазных границ. Рассчитаны константы параболического роста слоёв, что дало возможность предвидеть кинетику их роста и распределение азота в диффузионной зоне. Экспериментально обнаружена микроструктурная эволюция диффузионной зоны (после времени обработки 1 и 5 часов), которая обусловлена фазово-структурными превращениями во время диффузии азота.
Аналітично й експериментально досліджено процес високотемпературного азотування (Т = 950°C) титану. Відображено роль азоту як α-стабілізатора у формуванні нітридного шару та тришарової дифузійної зони (шар α-фази, шар α+β-фази і шар β-фази). Одержано наближений розв’язок сформульованої задачі щодо дифузії азоту в такому неоднорідному середовищі з урахуванням переміщень міжфазних меж. Розраховано константи параболічного росту шарів, що уможливило передбачити кінетику їх росту і розподіл азоту в дифузійній зоні. Експериментально зафіксовано еволюцію мікроструктури газонасиченого шару (після витримок у 1 і 5 годин), зумовлену структурно-фазовими перетвореннями під час дифузії азоту.
|
| issn |
1024-1809 |
| url |
https://nasplib.isofts.kiev.ua/handle/123456789/106996 |
| citation_txt |
Diffusion of Nitrogen and Phase—Structural Transformations in Titanium / O. Tkachuk, Ya. Matychak, I. Pohrelyuk, V. Fedirko // Металлофизика и новейшие технологии. — 2014. — Т. 36, № 8. — С. 1079-1089. — Бібліогр.: 6 назв. — англ. |
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2025-11-25T22:33:18Z |
| last_indexed |
2025-11-25T22:33:18Z |
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1850566658962227200 |
| fulltext |
1079
PACS numbers: 64.75.Nx, 66.30.Dn, 66.30.je, 68.35.Dv, 81.65.Lp
Diffusion of Nitrogen and Phase—Structural Transformations
in Titanium
O. Tkachuk, Ya. Matychak, I. Pohrelyuk, and V. Fedirko
G. V. Karpenko Physico-Mechanical Institute, N.A.S. of Ukraine,
5 Naukova Str.,
79601 Lviv, Ukraine
The process of high-temperature nitridation (Т 950С) of titanium is inves-
tigated analytically and experimentally. The role of nitrogen as -stabilizer in
forming of nitride layer and diffusion zone, which contains three layers (layer
of -phase, layer of -phase, and layer of -phase), is shown. The approxi-
mate solution of formulated task is obtained for diffusion of nitrogen in such
a heterogeneous medium, taking into account the motion of interfaces. The
constants of parabolic growth of layers are calculated. It allows foreseeing the
kinetics of their growth and distribution of nitrogen in diffusion zone. The
microstructure evolution of diffusion zone (after processing times of 1 h and 5
h), which is caused by the phase—structural transformations during diffusion
of nitrogen, is fixed experimentally.
Аналітично й експериментально досліджено процес високотемпературно-
го азотування (Т 950С) титану. Відображено роль азоту як -
стабілізатора у формуванні нітридного шару та тришарової дифузійної зо-
ни (шар -фази, шар -фази і шар -фази). Одержано наближений
розв’язок сформульованої задачі щодо дифузії азоту в такому неоднорід-
ному середовищі з урахуванням переміщень міжфазних меж. Розраховано
константи параболічного росту шарів, що уможливило передбачити кіне-
тику їх росту і розподіл азоту в дифузійній зоні. Експериментально зафік-
совано еволюцію мікроструктури газонасиченого шару (після витримок у
1 і 5 годин), зумовлену структурно-фазовими перетвореннями під час ди-
фузії азоту.
Процесс высокотемпературного азотирования (Т 950С) исследован ана-
литически и экспериментально. Отображена роль азота как -стабили-
затора в формировании нитридного слоя и трёхслойной диффузионной зо-
ны (слой -фазы, слой -фазы и слой -фазы). Получено приближенное
решение сформулированной задачи относительно диффузии азота в такой
неоднородной среде с учётом перемещения межфазных границ. Рассчита-
ны константы параболического роста слоёв, что дало возможность предви-
Металлофиз. новейшие технол. / Metallofiz. Noveishie Tekhnol.
2014, т. 36, № 8, сс. 1079—1089
Оттиски доступны непосредственно от издателя
Фотокопирование разрешено только
в соответствии с лицензией
2014 ИМФ (Институт металлофизики
им. Г. В. Курдюмова НАН Украины)
Напечатано в Украине.
1080 O. TKACHUK, Ya. MATYCHAK, I. POHRELYUK, and V. FEDIRKO
деть кинетику их роста и распределение азота в диффузионной зоне. Экс-
периментально обнаружена микроструктурная эволюция диффузионной
зоны (после времени обработки 1 и 5 часов), которая обусловлена фазово-
структурными превращениями во время диффузии азота.
Keywords: nitridation of titanium, kinetics, diffusion, phase—structural
transformations.
(Received October 10, 2013)
1. INTRODUCTION
It is necessary to have comprehensive knowledge (experimental and
theoretical) about the kinetics of the processes of interaction of ele-
ments taking into consideration the influence of process parameters
and phase—structural state of the material for forecasting of surface
strengthening of titanium alloys after nitriding. Titanium undergoes
polymorphic transformation at T 882
С [1]. Previously, it was in-
vestigated the kinetics of nitriding of titanium and ( )-titanium
alloys at temperatures of T T analytically and experimentally
[2].The microstructural evolution during -phase transformation
because of migration of -stabilizers is presented in [3]. However, the
authors did not take into consideration the role of nitrogen as -
stabilizer in the structural transformations. The influence of nitrogen
as -stabilizer during nitriding of titanium at temperatures of
T T under the rarefied atmosphere without forming of continuous
nitride layer on the surface was investigated earlier in [4]. The aim of
this work is to create the physical and mathematical model for diffu-
sion saturation of titanium at temperatures T T under medium
with high nitrogen potential; establish the kinetic peculiarities of such
nitriding analytically and experimentally caused by the phase-
structural transformations in the diffusion zone.
2. THERMODYNAMIC ANALYSIS
According to the phase diagram (Fig. 1), titanium undergoes polymor-
phic transformation (change of crystal lattice from h.c.p. to b.c.c.) at
T 882
С [5]. We will be interested in high-temperature (T T)
interaction of titanium with the gaseous medium with the high nitro-
gen potential. Under these conditions, according to the phase diagram
(Fig. 1), titanium nitrides (TiN, Ti2N) as products of chemical reac-
tions and solid solutions of nitrogen in - and -phases because of dif-
fusion dissolution of nitrogen in titanium matrix and structural trans-
formations are stable in the system. In particular, in the nitrogen con-
centration range 0 CN C23, solid solution of nitrogen in -phase is
DIFFUSION OF N AND PHASE—STRUCTURAL TRANSFORMATIONS IN Ti 1081
stable, while in the concentration range C12 CN C1S, solid solution of
nitrogen in -phase, and in the concentration range C23 CN C12, solid
solutions of nitrogen in both - and -phases can coexist.
It should be noted that in -phase the solubility of nitrogen is high
enough at temperature of nitriding and can reach, for example, for
Т 950
С 17.5 at.% against 0.75 at.% in -phase. At the same time,
coefficient of diffusion of nitrogen in -phase is on two-three orders
less than in -phase (Fig. 1).
3. PHYSICO-MATHEMATICAL MODEL
Let us consider the process of isothermal saturation of titanium at
temperatures higher than temperature of polymorphic transformation
(T T). In this case, the initial microstructure of titanium has -
modification. According to the thermodynamic analysis, the following
scheme of the nitrated surface layer of titanium is suggested (Fig. 2).
During the interaction of titanium with nitrogen, nitride layer (0
x Y0()) and diffusion zone are formed. The diffusion zone consists
of three layers. The layer І (Y0() x Y1()), which borders on the ni-
tride layer, is -phase of titanium significantly nitrogen-enriched be-
cause of high solubility of the nitrogen in -phase of titanium. This
layer is formed and it grows during nitriding because of diffusion dis-
solution of nitrogen and structural transformations in titanium, be-
cause nitrogen is -stabilizer. The layer III (Y2() x ), which bor-
ders on the titanium matrix, at the temperature of saturation, is -
phase of titanium enriched by nitrogen. Between the first and third
layers, the layer II (Y1() x Y2()), which is the disperse mixture of
Fig. 1. Titanium—nitrogen phase diagram [5].
1082 O. TKACHUK, Ya. MATYCHAK, I. POHRELYUK, and V. FEDIRKO
- and -phases enriched by nitrogen, is formed, and it grows.
It will be done some model assumptions for analytical description of
the process of nitriding. The aim of nitriding of titanium samples is
strengthening of their surface layers and the object of analytical inves-
tigation of the kinetics of diffusion saturation of titanium by nitrogen
the half-space (0 x ) has been chosen. Nitride film is formed im-
mediately on titanium surface, and the surface nitrogen concentration
does not change with time and corresponds to stoichiometric titanium
nitride (TiN). On the interfaces, the nitrogen concentrations corre-
sponding to equilibrium phase diagram are constant (Fig. 1).
The diffusion process in such heterogeneous system will be de-
scribed by Fick’s system of equations:
2
2
( , ) ( , )
,i i
i
C x C x
D
x
i 0, 1, 2, 3. (1)
Here, Сі(x, ) is nitrogen concentration, х is spatial coordinate, is
time, Di is nitrogen diffusion coefficient; index i 0 corresponds to
TiNx layer (0 x Y0()), i 1–-Ti layer (Y0() x Y1()), i 2–
( )-Ti-layer (Y1() x Y2()), i 3–-Ti layer (Y2() x )). It
should be noted that diffusion coefficient D2 is the averaged effective
diffusion coefficient of nitrogen in ( )-Ti layer [2].
Initial conditions ( 0):
Ci(x, 0) 0, Yi(0) 0 for x 0. (2)
Boundary conditions ( 0):
0 0 3 0 0 01 1 0 1
(0, ) , ( , ) 0, ( ), , ( ), ,S SС C С С Y C С Y C (3)
Fig. 2. Scheme of distribution of nitrogen concentration at nitriding of tita-
nium at temperature of T T.
DIFFUSION OF N AND PHASE—STRUCTURAL TRANSFORMATIONS IN Ti 1083
1 1 2 1 12 2 2 3 2 23
( ), ( ), , ( ), ( ), .С Y С Y C С Y С Y C
The motion of interfaces will be set by the parabolic dependences:
0 0 0 1 1 1 2 2 2
( ) 2 , ( ) 2 , ( ) 2Y D Y D Y D . (4)
Here, j (j 0, 1, 2) are dimensionless constants (for the specific tem-
perature), which will be determined from the law of conservation of
mass on the interfaces. Thus, for diffusion fluxes on the interfaces
Yj(), there are as follow:
00
1 1 2 2
0 01
0 1 01 1
( ) 0( ) 0
31 2 2
1 2 2 3
( ) 0 ( ) 0 ( ) 0 ( ) 0
( )
( ) ,
, .
S
x Yx Y
x Y x Y x Y x Y
C dYC
D D C C
x x d
CC C C
D D D D
x x x x
(5)
It is difficult to solve the diffusion task (1)—(5) in analytical form.
The method of approximate solution of above-mentioned task [6]
should be used. The linear distribution laws of the nitrogen concentra-
tions in nitride layer and in the first two layers of diffusion zone corre-
sponded to the quasi-stationary state is accepted, and Gauss law for the
distribution of nitrogen in the third layer is:
0 0 0 01
0
0
1 1 1 12
1 0
1
2 12 12 23
2 1
2
3 23
3
( , ) ( ) ,
( )
( )
( , ) ( ) ,
( ) ( )
( )
( , ) ( ) ,
( ) ( )
( )
( , ) .
2
S S
S S
x
C x C C C
Y
x Y
C x C C C
Y Y
x Y
C x C C C
Y Y
x Y
C x C erfc
D
(6)
The chosen functions Сі(x, ) satisfy the initial (2), boundary condi-
tions (3) and the differential equations (1). The following set of tran-
scendental equations for calculating the parameters j (j 0, 1, 2) was
obtained by the conditions of mass balance on interfaces (5) and rela-
tion (4):
0 1 0 0 2 1 1
0 0 1 0 1 0 0 2 1 2 1 1 3 2
2( )1 1
1, 1, 1.
2 ( ) ( )
A
A A A
(7)
Having solved the set of equations (7), we obtain:
1084 O. TKACHUK, Ya. MATYCHAK, I. POHRELYUK, and V. FEDIRKO
2
0 0 0 1 0 0 2 3 1 2
2 1 1 3 2
( 2/ ) /2, /2,
/2,
A B A B A A
A
(8)
where
1 2 3 0 1 2 0 0 1 1 1 2 2 2 3
0 01 0 01 1 12 12 23
0 1 2 3
01 1 1 12 12 23 23
1/( ), / , / , / ,
, , , .S S S
S S
B A A A D D D D D D
C C C C C C C C
A A A A
C C C C C C C
It should be noticed that parameters j depend on the values of nitrogen
concentrations on interfaces and its diffusion coefficients, which in
turn depend on the temperature. Taking the values of these parame-
ters, which correspond to the saturation temperature Т 950
С, ac-
cording to relations (8), the constants j (j 0, 1, 2): 0 0.183,
1 1.691, 2 0.782 were calculated. The following values of diffu-
sion coefficients were used here: D0 DТіN 310
12
cm
2/s, D1 D
2.510
9
cm
2/s, D2 10D1 (from those reasonings that D1 D2 D3),
D3 D 3.210
8
cm
2/s [1, 5], and such values of nitrogen concentra-
tions on interfaces: C0S 50, C01 33, C1S 17.5, C12 1.5, C23 0.75
(аt.%) (Fig. 1). Taking into consideration the correlation (4), the mo-
tion of interfaces will be presented as:
0 0 1 1 2 2
( ) , ( ) , ( ) ,Y K Y K Y K (9)
where
1/2 1/2 1/2
0 0 0 1 1 1 2 2 2
2 , 2 , 2K D K D K D – constants of the
parabolic growth of nitride layer and -, ( )-layers of diffusion
zone stabilized by nitrogen, respectively. In particular, these con-
stants for saturation temperature Т 950
С are such as
K0 6.3310
7
cm/s1/2, K1 5.3510
5
cm/s1/2, K2 7.810
5
cm/s1/2. (10)
Having found the constants of parabolic growth of the layers (10)
and having used the relations (9), it is easy to foresee the kinetics of
motion of interfaces (Fig. 3, a, b), and also time dependences of the
change of thickness of nitride layer (Fig. 3, a) and -, ( )- and -
layers of the diffusion zone (Fig. 3, c) in accordance with correlations:
0 0
1 1 0 1
2 2 1 2
( ) ( ),
( ) ( ) ( ) ,
( ) ( ) ( ) ,
Y Y
Y Y Y K
Y Y Y K
(11)
where 1 1 0 2 2 1
,K K K K K K .
DIFFUSION OF N AND PHASE—STRUCTURAL TRANSFORMATIONS IN Ti 1085
It should be noted that layer of diffusion zone is identified by the
motion of conventional boundary with the specific nitrogen concentra-
tion, for example С33 0.25 аt.%. Based on relations (6), the concen-
tration profiles of nitrogen in the diffusion zone of titanium after ni-
triding during 1 and 5 hours (Fig. 4) are calculated. It is clear that, ac-
cording to the assumptions (4) with the increase of processing time,
the motion of interfaces (Fig. 3, a, b) and, correspondingly, the growth
of thickness of the different layers of the diffusion zone (Fig. 3, с) oc-
cur, according to the parabolic dependences proportionally to the cor-
responding constants of parabolic growth Kj і j
K .
The diffusion coefficient of nitrogen in -phase is on two-four or-
ders higher than that in -phase and nitride layer that is why the
thickness of layer is much larger than the thickness of the other lay-
ers of diffusion zone (Fig. 3, а, с). If the thickness of nitride layer
(Y0()) is less than 0.2% from the total thickness of diffusion zone
(Y3()), the thickness of -, -, and -layers will be 16, 8 and 76%.
Fig. 3. Kinetics of motion of interfaces: interface of nitride layer Y0() (а); 1–
interface Y1(), 2–Y2(), 3–Y3(), – experiment (b); change of thickness of
layers: 1–thickness of -layer, 2–( )-layer, 3–-layer at nitriding of
titanium at Т 950
С (с).
1086 O. TKACHUK, Ya. MATYCHAK, I. POHRELYUK, and V. FEDIRKO
At the same time, the different solubility of nitrogen in - and -
phases of titanium influences on the distribution of nitrogen in the
diffusion zone. If the phase—structural transformations do not take
place in the diffusion zone, the profile of nitrogen in this zone would
have a small gradient because of the low solubility of nitrogen in -
phase. In fact, nitrogen, being -stabilizer, stimulates the -phase
transformations in the layers of the diffusion zone, adjacent to the ni-
tride layer. As the solubility of nitrogen in -phase is much higher
than that in -phase, we can foresee that, in zone I, the profile of nitro-
gen will have a large gradient (Fig. 4) as well as the distribution of mi-
crohardness in this zone. It has been confirmed by the experimental
investigations data.
4. EXPERIMENTAL PROCEDURE
Commercially pure (c.p.) titanium with dimensions of 10154 mm3
was investigated. The samples are polished (Rа 0.4 m) and washed
with deionized water before the treatment. The samples are heated to
the nitriding temperature in vacuum of 10
3
Pa. Then, they are satu-
rated with molecular nitrogen of the atmospheric pressure at the tem-
perature of 950С. The isothermal exposure in nitrogen was 1 and 5 h.
After isothermal exposure, the samples were cooled in nitrogen to
room temperature.
The microstructure of the nitride layers was studied using
‘EPIQUANT’ metallography microscope. Distribution of microhard-
ness on cross section of surface layers of c.p. titanium after nitriding
is estimated by measurement of microhardness at loading of 0.49 N.
Fig. 4. Concentration profiles of nitrogen in diffusion zone of titanium after
its nitriding at Т 950
С for two isothermal exposures: 1– 1 h, 2– 5 h.
DIFFUSION OF N AND PHASE—STRUCTURAL TRANSFORMATIONS IN Ti 1087
5. RESULTS AND DISCUSSION
The nitride layer of goldish colour is formed on the surface of c.p. tita-
nium after nitriding. Its colour is darkening with the increase of iso-
thermal exposure in nitrogen atmosphere. It indicates the increase of
its thickness.
The diffusion zone is formed under titanium nitride layer (Fig. 5). It
is difficult to find the layer II (Fig. 2) in this zone, which, according to
the phase diagram (Fig. 1), probably has to form. However, two differ-
ent parts, according to the structure of diffusion zone (zone A and zone
В) are clearly fixed. Zone A is -phase of titanium formed during ni-
triding by nitrogen as -stabilizer. Its thickness, according to data of
metallography analysis, increases from 20 to 45 m with the increase
of duration of nitriding from 1 to 5 h. Zone B is -phase of titanium on
the basis of solid solution of nitrogen, however formed as a result of
-transformation at cooling.
The results of investigation of character of microhardness distribu-
tion on cross section of surface layers of c.p. titanium after nitriding
are presented in Fig. 6. On curves of microhardness, distribution zone
A (layer I, Fig. 2) and zone B (probably, layer ІІ layer ІІІ, Fig. 2) are
clearly seen.
The large gradient of microhardness is typical for zone A. It is
caused by -transformation because of saturation by nitrogen as -
stabilizer and its comparatively high solubility in -phase. With the
increase of distance from the surface, the microhardness is drastically
decreases (Fig. 6) that is explained by the decrease of nitrogen concen-
tration (Fig. 4). The hardness of zone B is considerably less than that of
zone A because of large difference of nitrogen solubility in - and -
phases. The thickness of these zones is increased with the increase of
duration of nitriding (Fig. 6). In particular, the thickness of zone A is
Fig. 5. Structure of surface layers of c.p. titanium after nitriding at 1 h (а)
and 5 h (b) (Т 950С, p 105 Pа).
1088 O. TKACHUK, Ya. MATYCHAK, I. POHRELYUK, and V. FEDIRKO
34 m for 1 h and 69 m for 5 h. It will be noticed that this thick-
ness is larger than corresponding thickness, determined by the data of
metallography analysis. The general depth of diffusion zone (zone
A zone В) is 185 m for 1 h and 425 m for 5 h (Fig. 3, b).
The obtained analytical distribution of nitrogen (Fig. 4) and results
of measuring of microhardness (Fig. 6) confirm the correlation be-
tween model calculations and experimental data.
6. CONCLUSIONS
The kinetic peculiarities of diffusion saturation of titanium at temper-
ature of T 950С, which is higher than the temperature of -
polymorphic transformation, are determined analytically and experi-
mentally.
The role of nitrogen as -stabilizer in forming of multilayer diffu-
sion zone is shown.
The analytical calculations of the kinetics of the layers of diffusion
zone growth and the distribution of nitrogen in them correlate with the
results of experimental investigations. The microstructure evolution
(after processing times of 1 and 5 h) of the diffusion zone is fixed ac-
cording to them.
REFERENCES
1. V. M. Fedirko and I. M. Pohrelyuk, Azotuvannya Tytanu ta Yogo Splaviv
(Nitridation of Titanium and Its Alloys) (Kyiv: Naukova Dumka: 1995) (in
Ukrainian).
2. Ya. Matychak, V. Fedirko, I. Pohrelyuk, O. Yaskiv, and O. Tkachuk, Defect
Fig. 6. Distribution of microhardness on cross section of surface layers of c.p.
titanium after nitriding at 1 h (1) and 5 h (2) (Т 950С, p 105
Pа).
DIFFUSION OF N AND PHASE—STRUCTURAL TRANSFORMATIONS IN Ti 1089
Diffus. Forum, 277: 33 (2008).
3. I. Katzarov, S. Malinov, and W. Sha, Metall. Mater. Trans. A, 33A: 1027
(2002).
4. Ya. Matychak, V. Fedirko, I. Pohrelyuk, and O. Tkachuk,
Diffusion-Fundamentals Org., 11, No. 48: 1 (2009).
5. E. Fromm und E. Gebhardt, Gase und Kohlenstoff in Metallen. Reine und
angewandte Metallkunde in Einzeldarstellungen. Bd. 26 (Berlin—Heidelberg—
New York: Springer-Verlag: 1976) (in German).
6. А. V. Lykov, Teoriya Teploprovodnosti (Theory of Thermal Conduction)
(Moscow: Vysshaya Shkola: 1966) (in Russian).
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/NLD (Gebruik deze instellingen om Adobe PDF-documenten te maken die zijn geoptimaliseerd voor prepress-afdrukken van hoge kwaliteit. De gemaakte PDF-documenten kunnen worden geopend met Acrobat en Adobe Reader 5.0 en hoger.)
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/ENU (Use these settings to create Adobe PDF documents best suited for high-quality prepress printing. Created PDF documents can be opened with Acrobat and Adobe Reader 5.0 and later.)
>>
/Namespace [
(Adobe)
(Common)
(1.0)
]
/OtherNamespaces [
<<
/AsReaderSpreads false
/CropImagesToFrames true
/ErrorControl /WarnAndContinue
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/IncludeNonPrinting false
/IncludeSlug false
/Namespace [
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(InDesign)
(4.0)
]
/OmitPlacedBitmaps false
/OmitPlacedEPS false
/OmitPlacedPDF false
/SimulateOverprint /Legacy
>>
<<
/AddBleedMarks false
/AddColorBars false
/AddCropMarks false
/AddPageInfo false
/AddRegMarks false
/ConvertColors /ConvertToCMYK
/DestinationProfileName ()
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/Downsample16BitImages true
/FlattenerPreset <<
/PresetSelector /MediumResolution
>>
/FormElements false
/GenerateStructure false
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/MultimediaHandling /UseObjectSettings
/Namespace [
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(CreativeSuite)
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]
/PDFXOutputIntentProfileSelector /DocumentCMYK
/PreserveEditing true
/UntaggedCMYKHandling /LeaveUntagged
/UntaggedRGBHandling /UseDocumentProfile
/UseDocumentBleed false
>>
]
>> setdistillerparams
<<
/HWResolution [2400 2400]
/PageSize [612.000 792.000]
>> setpagedevice
|