Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment
The aim of the study was to improve the lamellar structure and wear resistance of arc-sprayed coatings. FeNiCrAl arc-sprayed coatings were remelted by the tungsten inert gas welding method. The as-sprayed and remelted specimens were subjected to comparative structural phase composition examina...
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Інститут проблем міцності ім. Г.С. Писаренко НАН України
2014
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| Назва видання: | Проблемы прочности |
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| Цитувати: | Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment / H.L. Tian, S.C. We, Y.X. Chen, H. Tong, Y. Liu, B.S. Xub // Проблемы прочности. — 2014. — № 2. — С. 90-97. — Бібліогр.: 12 назв. — англ. |
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irk-123456789-1127142020-12-20T14:49:43Z Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment Tian, H.L. We, S.C. Chen, Y.X. Tong, H. Liu, Y. Xub, B.S. Научно-технический раздел The aim of the study was to improve the lamellar structure and wear resistance of arc-sprayed coatings. FeNiCrAl arc-sprayed coatings were remelted by the tungsten inert gas welding method. The as-sprayed and remelted specimens were subjected to comparative structural phase composition examination using optical microscopy, scanning electron microscopy and X-ray diffraction. Additionally, the effect of the remelting treatment on the wear mechanism of the arc sprayed coatings was also studied. It was found from the experiments that the tungsten inert gas surface process has the potential to form pore- and crack-free coatings. Further investigations showed that the dominant mechanism of wear for the as-sprayed coatings was oxide delamination and for the tungsten inert gas remelted coatings was cutting and ploughing Усовершенствованы пластинчатая структура и износостойкость покрытий, полученных электродуговой металлизацией. С помощью дуговой сварки вольфрамовым электродом в среде инертного газа проведена переплавка покрытий на основе FeNiCrAl, полученных электро-дуговой металлизацией. С использованием методов оптической микроскопии, растровой электронной микроскопии и дифракции рентгеновских лучей осуществлено сравнительное исследование структуры и фазового состава напыленных и переплавленных покрытий. Изучено влияние обработки путем переплавки на механизм износа покрытий, полученных электро-дуговой металлизацией. Установлено, что реализация дуговой сварки вольфрамовым электродом в среде инертного газа позволяет разрабатывать покрытия без пор и трещин. Даль- нейшие исследования показали, что основной признак износа покрытий, полученных электро-дуговой металлизацией, – расщепление оксида, в то время как покрытий, переплавленных с помощью дуговой сварки вольфрамовым электродом в среде инертного газа, – резание и пропахивание. Удосконалено пластинчасту структуру та зносостійкість покриттів, отриманих електро-дуговою металізацією. За допомогою дугового зварювання вольфрамовим електро-дом у середовищі інертного газу проведено переплавку покриттів на основі FeNiCrAl, отриманих електродуговою металізацією. Із використанням методів оптичної мікроскопії, растрової електронної мікроскопії та дифракції рентгенівських променів проведено порівняльне дослідження структури і фазового складу напилених і переплавлених покриттів. Вивчено вплив обробки шляхом переплавки на механізм зношення покриттів, отриманих електродуговою металізацією. Установлено, що реалізація дугового зварювання вольфрамовим електродом у середовищі інертного газу дозволяє розробляти покриття без пор і тріщин. Подальші дослідження показали, що основними ознаками зношення покриттів, отриманих електродуговою металізацією, є розщеплення оксиду, в той час як покриттів, переплавлених за допомогою дугового зварювання вольфрамовим електродом у середовищі інертного газу, – різання і проорювання 2014 Article Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment / H.L. Tian, S.C. We, Y.X. Chen, H. Tong, Y. Liu, B.S. Xub // Проблемы прочности. — 2014. — № 2. — С. 90-97. — Бібліогр.: 12 назв. — англ. 0556-171X http://dspace.nbuv.gov.ua/handle/123456789/112714 539.4 en Проблемы прочности Інститут проблем міцності ім. Г.С. Писаренко НАН України |
| institution |
Digital Library of Periodicals of National Academy of Sciences of Ukraine |
| collection |
DSpace DC |
| language |
English |
| topic |
Научно-технический раздел Научно-технический раздел |
| spellingShingle |
Научно-технический раздел Научно-технический раздел Tian, H.L. We, S.C. Chen, Y.X. Tong, H. Liu, Y. Xub, B.S. Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment Проблемы прочности |
| description |
The aim of the study was to improve the
lamellar structure and wear resistance of
arc-sprayed coatings. FeNiCrAl arc-sprayed
coatings were remelted by the tungsten inert gas
welding method. The as-sprayed and remelted
specimens were subjected to comparative structural
phase composition examination using optical
microscopy, scanning electron microscopy
and X-ray diffraction. Additionally, the effect
of the remelting treatment on the wear mechanism
of the arc sprayed coatings was also studied.
It was found from the experiments that the
tungsten inert gas surface process has the potential
to form pore- and crack-free coatings. Further
investigations showed that the dominant
mechanism of wear for the as-sprayed coatings
was oxide delamination and for the tungsten
inert gas remelted coatings was cutting and
ploughing |
| format |
Article |
| author |
Tian, H.L. We, S.C. Chen, Y.X. Tong, H. Liu, Y. Xub, B.S. |
| author_facet |
Tian, H.L. We, S.C. Chen, Y.X. Tong, H. Liu, Y. Xub, B.S. |
| author_sort |
Tian, H.L. |
| title |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment |
| title_short |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment |
| title_full |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment |
| title_fullStr |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment |
| title_full_unstemmed |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment |
| title_sort |
microstructure and wear resistance of an arc-sprayed fe-based coating after surface kemelting treatment |
| publisher |
Інститут проблем міцності ім. Г.С. Писаренко НАН України |
| publishDate |
2014 |
| topic_facet |
Научно-технический раздел |
| url |
http://dspace.nbuv.gov.ua/handle/123456789/112714 |
| citation_txt |
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating after Surface Kemelting Treatment / H.L. Tian, S.C. We, Y.X. Chen, H. Tong, Y. Liu, B.S. Xub // Проблемы прочности. — 2014. — № 2. — С. 90-97. — Бібліогр.: 12 назв. — англ. |
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Проблемы прочности |
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2025-07-08T04:29:41Z |
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| fulltext |
UDC 539.4
Microstructure and Wear Resistance of an Arc-Sprayed Fe-Based Coating
after Surface Remelting Treatment
H. L. Tian,a,b,1 S. C. Wei,b Y. X. Chen,b H. Tong,b Y. Liu,b and B. S. Xub
a School of Materials Science and Engineering, Beijing University of Aeronautics and Astronautics,
Beijing, China
b National Key Laboratory for Remanufacturing, Academy of Armored Forces Engineering, Beijing,
China
1 haoliangtian@163.com
ÓÄÊ 539.4
Ìèêðîñòðóêòóðà è èçíîñîñòîéêîñòü ïîêðûòèÿ íà îñíîâå æåëåçà, ïîëó-
÷åííîãî ýëåêòðîäóãîâîé ìåòàëëèçàöèåé, ïîñëå îáðàáîòêè ïîâåðõíîñòè ñ
ïîìîùüþ ïåðåïëàâêè
Õ. Ë. Òèàíà,á,1, Ñ. Ö. Âåéá, É. Ê. ×åíá, Õ. Òîíãá, É. Ëèóá, Á. Ñ. Êñóá
à Ôàêóëüòåò ìàòåðèàëîâåäåíèÿ è ìàøèíîñòðîåíèÿ, Ïåêèíñêèé óíèâåðñèòåò àâèàöèè è êîñìî-
íàâòèêè, Ïåêèí, Êèòàé
á Íàöèîíàëüíàÿ ëàáîðàòîðèÿ ìîäåðíèçàöèè, Èíæåíåðíàÿ àêàäåìèÿ áðîíåòàíêîâûõ âîéñê, Ïåêèí,
Êèòàé
Óñîâåðøåíñòâîâàíû ïëàñòèí÷àòàÿ ñòðóêòóðà è èçíîñîñòîéêîñòü ïîêðûòèé, ïîëó÷åííûõ
ýëåêòðîäóãîâîé ìåòàëëèçàöèåé. Ñ ïîìîùüþ äóãîâîé ñâàðêè âîëüôðàìîâûì ýëåêòðîäîì â
ñðåäå èíåðòíîãî ãàçà ïðîâåäåíà ïåðåïëàâêà ïîêðûòèé íà îñíîâå FeNiCrAl, ïîëó÷åííûõ ýëåêòðî-
äóãîâîé ìåòàëëèçàöèåé. Ñ èñïîëüçîâàíèåì ìåòîäîâ îïòè÷åñêîé ìèêðîñêîïèè, ðàñòðîâîé
ýëåêòðîííîé ìèêðîñêîïèè è äèôðàêöèè ðåíòãåíîâñêèõ ëó÷åé îñóùåñòâëåíî ñðàâíèòåëüíîå
èññëåäîâàíèå ñòðóêòóðû è ôàçîâîãî ñîñòàâà íàïûëåííûõ è ïåðåïëàâëåííûõ ïîêðûòèé. Èçó÷å-
íî âëèÿíèå îáðàáîòêè ïóòåì ïåðåïëàâêè íà ìåõàíèçì èçíîñà ïîêðûòèé, ïîëó÷åííûõ ýëåêòðî-
äóãîâîé ìåòàëëèçàöèåé. Óñòàíîâëåíî, ÷òî ðåàëèçàöèÿ äóãîâîé ñâàðêè âîëüôðàìîâûì ýëåêòðî-
äîì â ñðåäå èíåðòíîãî ãàçà ïîçâîëÿåò ðàçðàáàòûâàòü ïîêðûòèÿ áåç ïîð è òðåùèí. Äàëü-
íåéøèå èññëåäîâàíèÿ ïîêàçàëè, ÷òî îñíîâíîé ïðèçíàê èçíîñà ïîêðûòèé, ïîëó÷åííûõ ýëåêòðî-
äóãîâîé ìåòàëëèçàöèåé, – ðàñùåïëåíèå îêñèäà, â òî âðåìÿ êàê ïîêðûòèé, ïåðåïëàâëåííûõ ñ
ïîìîùüþ äóãîâîé ñâàðêè âîëüôðàìîâûì ýëåêòðîäîì â ñðåäå èíåðòíîãî ãàçà, – ðåçàíèå è
ïðîïàõèâàíèå.
Êëþ÷åâûå ñëîâà: âûñîêîñêîðîñòíàÿ ýëåêòðîäóãîâàÿ ìåòàëëèçàöèÿ, ïðîöåññ ïåðåïëàâ-
êè, ìèêðîñòðóêòóðà, èçíîñ.
Introduction. The arc spraying process is widely used to prepare various thin
coatings, and is especially applied in the maintaining and rebuilding fields [1]. However,
the coatings obtained using this process exhibit lamellar microstructure, high porosity and
low surface hardness and their wear resistance is not sufficient for many applications [2].
Therefore, a surface remelting treatment needs to be carried out to reinforce the adhesive
strength and enhance the wear resistance of the as-sprayed coatings.
The reduction of microinclusion content of coatings by surface melting using processes
such as laser [3], plasma [4] and tungsten inert gas (TIG) [5] welding has been shown to
improve coating toughness owing to changes in microstructure, chemical composition and
© H. L. TIAN, S. C. WEI, Y. X. CHEN, H. TONG, Y. LIU, B. S. XU, 2014
90 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2
oxygen content. In recent years, several studies have been performed using the TIG method
[6]. The process increases surface hardness, improves wear resistance and results in little or
no distortion. In this work, the microstructural properties, hardness, phase composition and
wear resistance of Fe-based remelted coatings made using a TIG torch are reported.
Experimental Method. Fe–Ni–Cr–Al cored wire with a diameter of 2 mm was used
to produce as-sprayed coatings. The chemical composition of the arc spraying wire was
(wt.%): Ni�10, Cr� 5, Al� 5, B �1, Nb�1, Re�1, Fe – balance.
The wires were sprayed onto a grit blasted and degreased AISI 1045 steel substrate
with dimensions of 100 100 10� � mm using a self-designed HAS-02 wire arc gun system.
The process parameters were optimized as follows: spraying voltage 28 V, spraying current
160 A, compressed air pressure 0.7 MPa, standoff distance, 200 mm. The thickness of the
as-sprayed coatings was 400–500 �m and they were subsequently melted using a TIG
torch. The TIG torch/arc was produced with an operating current ranging from 80 to 100 A.
The remelting process was carried out at 3 and 4 mm/s speed and the electrode height
from the substrate surface was varied between 3 and 5 mm. The shield gas flow (argon)
was 12 l/min.
The microstructures and chemical compositions of cross sections of the as-sprayed
and remelted samples were compared using optical microscopy, scanning electron
microscopy (SEM) and energy dispersive spectroscopy (EDS). X-ray diffraction (XRD)
analysis was conducted to determine the phases formed in the surface alloyed layer.
Dry sliding wear tests were carried out using a ball-on-plate reciprocating machine at
room temperature (25�C). The counterpart ball was quenched before the wear test. The
abrading ball was a GCr15 ball with 65 HRC and of 4 mm in diameter. The applied load and
sliding distance were 50 N and 2700 mm (with an increment of 3 mm), respectively. The
sliding velocity was 3 mm/s. Five samples were measured for each set of test parameters.
The friction coefficient was monitored with a computer. The microstructures of worn
surfaces and wear debris were analyzed by SEM to understand the wear mechanism for the
coated and uncoated samples.
Results and Discussion.
X-Ray Diffraction. X-ray diffraction analysis was performed on the surface of the
as-sprayed and remelted coatings. The diffraction patterns are shown in Fig. 1a and 1b,
respectively. As can be seen from Fig. 1a, �-Fe, �-Fe and Fe–Al intermetallic compounds
are major phases present in the surface of the as-sprayed coating. Moreover, during
spraying, molten liquid drops are exposed to air and are oxidized in flight to the substrate,
and many oxides, such as Al2O3, Cr2O3, and Fe3O4, can be present at the exposed surfaces
of splats prior to the deposition of the subsequent layer [7].
Microstructure and Wear Resistance ...
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2 91
a b
Fig. 1. XRD results for as-sprayed (a) and remelted (b) coatings.
Figure 1b shows the phases of the remelted coating. These are mainly �-Fe, Fe–Al
intermetallic compounds, (Fe, Cr) solid solution and Cr23C6 carbides, and weak peaks are
assigned to Al2O3 oxides. These results clearly confirm that the elements Fe, Cr, Ni, and Al
dissolved in the coating matrix then formed more alloy phases, while few oxides were
detected in the coating after the TIG remelting process.
Microstructural Examination. A comparison was made of the cross-sectional
micrographs of the remelted coating formed by TIG (Fig. 2b) and the as-sprayed coating
(Fig. 2a). A thin white layer is observed at the interface in Fig. 2b, which indicates a good
metallurgical bonding between the remelted coating and the substrate.
At the bonding zone, an extremely high rate of heat transfer occurred between the
molten pool and the substrate and a large melt was obtained under cooling leading to a very
high rate of solidification [8]. The solid/liquid interface grew in a flat form giving rise to
the formation of a bright flat grain in the coating as shown in Fig. 2b.
H. L. Tian, S. C. Wei, Y. X. Chen, et al.
92 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2
Fig. 2. Optical micrographs of cross sections of the as-sprayed (a) and the remelted (b) coatings.
Fig. 3. SEM cross-sectional morphology of the as-sprayed (a) and the remelted (b) coatings and high
magnification morphology (c).
Figure 3a shows a cross-sectional SEM image of the as-sprayed coating before TIG
treatment. Laminated structures with many pores and cracks occur in the lamellar structure
and the interface between the coating and substrate. Figure 3b shows the cross-sectional
morphology of the remelted coating. In contrast to Fig. 3a, the remelted coating was
characterized by a more homogeneous structure, absence of structure lamination, and
decreased surface roughness and porosity. In order to analyze the porosities quantitatively,
a computer image analyzer was employed. It was observed that the porosities of the
as-sprayed coatings were 17–22% and the remelted coatings show a dramatically reduced
porosity of only 1.1–2.8%.
A typical patter of higher magnification morphology observed for remelted coatings
is shown in Fig. 3c. The SEM investigations revealed a distinct refinement of the structure.
No microcracks delaminating the remelted coating were observed. Depending on the material
cooling rate function of the adopted treatment parameters, different phase morphologies
were observed of which microdendrite and cellular–dendrite were predominant.
Microhardness Investigations. The microhardness profiles of the as-sprayed and
remelted coatings with coating depth are shown in Fig. 4. It can be seen that the
microhardness of the as-sprayed coating gradually increased with increasing distance from
the substrate to the coating surface. The hardness of the as-sprayed coating was about
480–580 HV0.1. The anisotropy of the coating, resulting from the characteristic layered
structure of the as-sprayed material, was responsible for the microhardness values and their
distributions.
The hardness increased to about 670–740 HV0.1 for the as-sprayed coating after
remelting treatment. This result confirms that there are marked differences in the micro-
structures of the coatings before and after the TIG remelting process. The remelted coating
exhibits a high hardness corresponding to hard phases such as intermetallic compounds and
(Fe, Cr) solid solution distributed in the dense structure and homogeneous chemical
dispersion as well as recrystallization.
Wear Resistance Performance. Comparing the substrate, as-sprayed coating and TIG
remelted coating, the variations of friction coefficient are shown in Fig. 5. The average
friction coefficient values of the substrate, as-sprayed coating and remelted coating were
calculated as 0.9, 0.6, and 0.5, respectively. It can be seen that the TIG remelted coating is
more effective in improving wear resistance, and its friction coefficient curve shows a
smooth variation. Also, the friction coefficient curve of the remelted coating is more stable
than that of the substrate with increasing sliding distance.
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2 93
Microstructure and Wear Resistance ...
Fig. 4. Microhardness of the as-sprayed and remelted coatings.
In order to compare the wear resistance of the as-sprayed coating and the remelted
one, SEM examinations of the worn surfaces were undertaken, as shown in Fig. 6. It can be
seen that the wear track of the remelted coating (Fig. 6c) is shallower than those of the
as-sprayed coating (Fig. 6b) and the substrate (Fig. 6a). Also, the wear volume losses for
the substrate, as-sprayed coating and remelted coating were measured as 3 78 10 6. � ,
2 46 10 6. ,� and 113 10 6. � �m3, respectively, revealing that the TIG remelted coating has
the lowest wear volume for the dense microstruture. A fine cellular structure was formed
after the TIG remelting process.
94 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2
H. L. Tian, S. C. Wei, Y. X. Chen, et al.
Fig. 5. Friction coefficients of the Fe-based coatings and substrate.
Fig. 6. Macrographics wear tracks of the substrate (a), the as-sprayed (b) and the remelted (c)
coatings.
Aiming to understand the wear mechanisms of the as-sprayed and remelted coatings,
SEM and EDS analyses of the wear surface and wear debris were undertaken, as shown in
Figs. 7 and 8, respectively. The EDS examinations of the wear tracks of the as-sprayed
coating confirmed that the chemical composition of the micro-zone of the wear surface is
mainly 68.38 wt.% Fe, 9.28 wt.% Al, 21.13 wt.% O, and 1.21 wt.% Nb (Fig. 7b). The
results show the presence of iron oxides on practically all the surfaces of the coatings that
were tested (Fig. 7a). The concentration of these oxides fell as the sliding distance
increased. This can be explained by the low cohesive strength among splats, numerous
pores and microcracks already present in the as-sprayed coating or generated during the
tests carried out. Under the dry sliding conditions, the induced strong shearing stress
initiates microcracks, which, together with inherent microcracks, grow and extend along
the boundaries of the splats. When the stress intensity is close to the fracture toughness of
the coating, complete splats should break off from the coating [9].
The wear surface of the remelted coating is distinguished by discontinuous parallel
grooves (see mark-up spectrum 2 in Fig. 8a), which form as the hard abrasive phases dig
into the worn coating surface and then plough out the matrix material from the groove to
the side. This causes the so-called grooving wear mode [10]. Therefore, cutting and
ploughing are the main abrasive wear mechanisms. But, the distribution of the (Fe, Cr)
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2014, ¹ 2 95
Microstructure and Wear Resistance ...
a
Fig. 7. SEM and EDS analyzes of the as-sprayed coating: (a) SEM morphology of the wear track;
(b) EDS analysis of the wear track.
a
b
b
Fig. 8. SEM and EDS analyzes of the remelted coating: (a) SEM morphology of the wear track;
(b) EDS analysis of the wear track.
solid solution and Cr23C6 hard phases surrounded by a matrix of �-Fe will be of benefit for
improving the wear resistance. The surrounding ductile structure (�-Fe) will absorb energy,
while the coating bears a high load, releasing the residual stress [11]. This structural
characteristic of abrasive particles embedded in the ductile matrix will prevent the
microcracks often initiated from inside of the oxide boundaries with the action of
concentrated stresses and improve the wear resistance of the remelted coating. Furthermore,
oxygen atoms were not detected in the wear surface (Fig. 8b), which confirms that the
remelted coating has the ability to resist oxidation wear failure. The very dense micro-
structure and low porosity characteristics also prevent the abrasive particles from micro-
cutting the surface by breaking them up and causing them to lose their cutting function
[12]. Therefore, the coating has excellent abrasive wear resistance.
C o n c l u s i o n s
1. Coatings produced by TIG remelting of Fe-based alloy coatings are free from pores
and cracks and show good metallurgical bonding with the substrate. The primary phases of
the remelted coating were identified as Cr23C6 carbides and Fe-based solid solution.
2. The consequence of the remelting treatment is the transformation �-Fe
�-Fe. The
wear resistance of coated samples is far better than that of uncoated samples. Particles of
thin flake sheet form combined with the energy dispersive spectroscopic analysis confirm
that oxide delamination is the dominant wear mechanism of the as-sprayed coating. Cutting
and ploughing are the main abrasive wear mechanisms of the remelted coating.
Acknowledgements. The authors are grateful for the support provided by 973 Project
(2011CB013403), and the Natural Science Foundation of China (51105377, 50971132),
National Science and Technology Supporting Project (No. 2011baf11B07).
Ð å ç þ ì å
Óäîñêîíàëåíî ïëàñòèí÷àñòó ñòðóêòóðó òà çíîñîñò³éê³ñòü ïîêðèòò³â, îòðèìàíèõ åëåêòðî-
äóãîâîþ ìåòàë³çàö³ºþ. Çà äîïîìîãîþ äóãîâîãî çâàðþâàííÿ âîëüôðàìîâèì åëåêòðî-
äîì ó ñåðåäîâèù³ ³íåðòíîãî ãàçó ïðîâåäåíî ïåðåïëàâêó ïîêðèòò³â íà îñíîâ³ FeNiCrAl,
îòðèìàíèõ åëåêòðîäóãîâîþ ìåòàë³çàö³ºþ. ²ç âèêîðèñòàííÿì ìåòîä³â îïòè÷íî¿ ì³êðî-
ñêîﳿ, ðàñòðîâî¿ åëåêòðîííî¿ ì³êðîñêîﳿ òà äèôðàêö³¿ ðåíòãåí³âñüêèõ ïðîìåí³â ïðî-
âåäåíî ïîð³âíÿëüíå äîñë³äæåííÿ ñòðóêòóðè ³ ôàçîâîãî ñêëàäó íàïèëåíèõ ³ ïåðåïëàâ-
ëåíèõ ïîêðèòò³â. Âèâ÷åíî âïëèâ îáðîáêè øëÿõîì ïåðåïëàâêè íà ìåõàí³çì çíîøåííÿ
ïîêðèòò³â, îòðèìàíèõ åëåêòðîäóãîâîþ ìåòàë³çàö³ºþ. Óñòàíîâëåíî, ùî ðåàë³çàö³ÿ äóãî-
âîãî çâàðþâàííÿ âîëüôðàìîâèì åëåêòðîäîì ó ñåðåäîâèù³ ³íåðòíîãî ãàçó äîçâîëÿº ðîç-
ðîáëÿòè ïîêðèòòÿ áåç ïîð ³ òð³ùèí. Ïîäàëüø³ äîñë³äæåííÿ ïîêàçàëè, ùî îñíîâíèìè
îçíàêàìè çíîøåííÿ ïîêðèòò³â, îòðèìàíèõ åëåêòðîäóãîâîþ ìåòàë³çàö³ºþ, º ðîçùåïëåí-
íÿ îêñèäó, â òîé ÷àñ ÿê ïîêðèòò³â, ïåðåïëàâëåíèõ çà äîïîìîãîþ äóãîâîãî çâàðþâàííÿ
âîëüôðàìîâèì åëåêòðîäîì ó ñåðåäîâèù³ ³íåðòíîãî ãàçó, – ð³çàííÿ ³ ïðîîðþâàííÿ.
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Received 22. 11. 2013
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