Induction brazing of cermets to steel/Kermiste induktsioonjootmine terasega.
Laansoo, Andres ; Kubarsepp, Jakob ; Vainola, Vello 等
1. INTRODUCTION
Cermets, based on titanium and chromium carbides, have low density,
relatively high strength and wear resistance and also high oxidation and
corrosion resistance and therefore they can be successfully used in wear
resistant structural components. When abrasion is combined with
oxidation or chemical corrosion, the chromium carbide cermet is highly
superior to tungsten carbide hardmetal [1]. TiC-based cermets, cemented
with Ni or steel binder phase, applied in metal cutting and forming
operations [2], have been found to be superior over tungsten carbide
based hardmetals. TiC-Ni cermets, produced by self-propagating high
temperature synthesis, can be used for valves, tappets in engines, seals
or bearings [3-5].
To save expensive carbide composites and to simplify the design of
complicated tools and wear resistant components and to reduce the
manufacturing costs, bimetallic "cermet + steel" compounds can
be used. Durability of such bimetals depends on their mechanical
strength and internal residual stresses of the joints. Diffusion welding
can be successfully used for bimetallic "cermet + steel"
compounds as a shear strength up to 300 MPa can be achieved [6]. In
cutting tools production and in other applications, brazing as a bonding
technique has been commonly used. However, information concerning the
brazing of cermets to steel is comparatively restricted [3-8].
The shear strength of the 60%TiC + 40%Ni cermet, vacuum brazed with
Ag-Cu-Zn filler metal to structural steel, was reported in [3-5]. By
increasing silver content in the brazing filler metal (FM) from 23% to
46%, the shear strength increased from 95 up to 120 MPa. The mechanical
properties of the joints were very sensitive to the brazing temperature
and time and a 2 to 3 times decrease of them occurred when optimal
parameters were not used. In [7] the shear strength of the joints
"TiC-based cermet + steel" was studied and a maximum shear
strength of up to 110-130 MPa was achieved when an amorphous filler
metal was used [7]. Some preliminary results, related to the shear
strength of the chromium carbide based cermet, vacuum brazed to steel,
are reported in [8].
The brazing of two different materials, such as cermet to steel, is
apt to present numerous difficulties arising out of differences in their
chemical, physical and mechanical properties. To achieve the required
properties of the joints (strength, corrosion or oxidation resistance)
in specific service areas, the most important factors are the selection
of the optimal filler metal and process parameters (heating method,
brazing atmosphere, fluxes, temperature and time). To ensure the
oxidation and corrosion resistance of brazed joints, Ni- and also
Ag-based filler metals are usually recommended. New amorphous filler
metals (AFM), produced by rapid solidification technology, are
prospective due to their chemical composition. The industrial
application of these materials is still limited [9]. To ensure high
quality of the joints, relatively high vacuum ([10.sup.-2]-1.3 Pa) [10]
or protective atmosphere (Ar, [N.sub.2], Ar/[H.sub.2]) must be applied
during brazing.
Thin coatings of Ni or Cu interlayers [7] on the faying surfaces of
TiC-based cermets can protect the surfaces and improve wetting. A
significant increase, from 17% to 70%, in the shear strength of brazed
joints for one cermet grade was observed. For other grades the effect of
the Ni coating was negative, as the shear strength decreased by about
22%-25%.
Filler metals, containing titanium or Ti coatings, were used for
brazing ceramics because their properties improve the wetting of
ceramics [11-13] and reduce the oxidation of faying surfaces. Such
coatings are attractive also for brazing of the cermets. After
mechanical metallization of ceramics, conventional and inexpensive
filler metals can be used [12-13].
In many applications of brazing, induction heating is a faster and
more efficient technique than traditional vacuum furnace heating.
This paper aims to demonstrate the feasibility of induction heating
for vacuum and air brazing of chromium and titanium carbide based
cermets with traditional and amorphous filler metals. Focus is also on
the effect of thin coatings on the performance of joints "cermet +
steel".
2. MATERIALS AND EXPERIMENTAL PROCEDURE
The study focuses on the joints, based on chromium carbide base
cermets with Ni binder and titanium carbide base cermets with Ni-Mo and
Fe-Ni steel binder phase (Table 1). Hardmetal on the basis of WC with
15% Co-binder (Table 1) as a reference material was also tested. The
mean grain size of carbides of the TiC-based cermets was 2.0-2.2
[micro]m and of the [Cr.sub.3][C.sub.2]-based ones 3-4 [micro]m.
Specimens with the diameter of 18.0-19.6 mm and height of 10 mm were
used.
Carbon structural steel grade C 45 (0.45 wt% of carbon) and
austenitic stainless steel grade X10CrNi18-8 (1.4310) were used as
counterparts. The diameter of the counterparts was 20 mm and the height
was 50 mm. The cermet and steel counterparts to be bonded were ground to
surface finish of [R.sub.a] [less than or equal to] 1 [micro]m.
Brazing filler metals were selected (see Table 2) taking into
consideration the wetting ability of carbides as well as oxidation and
corrosion resistance. To ensure high oxidation and corrosion resistance,
especially for stainless steel-cermet joints, nickel and silver based
brazing alloys are preferred, but they are rather expensive. Cheaper
copper based filler metals, successfully used for the brazing of TiC
cermets to steel [7], were also used.
For vacuum brazing, four different amorphous filler metal foils
with the thickness of 50 [micro]m were selected. The amorphous filler
metals, containing titanium (grades S1201 and S1204), are compatible
with the carbide phase of TiC-cermets and Ni-based filler metals (grade
S1311) with the binder phase cermets. Ni-Co-Fe-Si amorphous filler metal
(grade S1311) was specially developed for vacuum brazing of tungsten
carbide based hardmetals [10]. Ni-Co based amorphous filler metal grade
MBF20, produced in large volumes [9], was tested for brazing of
TiC-based cermets to steel [7].
Traditional brazing filler metals were selected from the production
list of commercially available alloys, developed for brazing of WC-Co
hardmetals, especially for impact loadings (Table 2). Three grades of
brazing fluxes were tested and an optimal brazing flux grade F125 was
selected.
Some CrNi30 and TiC50/NiMo specimens were metallized with titanium
at Julich Research Centre (Germany). Specimens were clamped to the
spindle of a lathe by a chuck. The rotating Ti brushes passed the
surface of the cermet and due to the wear of brushes coated them with a
film of titanium. The mean thickness of the coatings was 5 [micro]m. A
portable electrochemical metallizing system was used to deposit the 10
(m thick Ag or Ni coating on the cermet surface.
The brazing processes were conducted in the special equipment UDS-4
in vacuum (0.8-1.0 Pa) or in the air environment (Fig. 1). The foils of
amorphous filler metals with a thickness of 50 [micro]m and traditional
filler metals with a thickness of 150 m[micro] were placed between the
cermet-steel parts under low pressure (2-3 MPa) and were induction
heated for 1 min. The pressure, applied to the specimen, was achieved by
a hydraulic system. Joints were heated by the induction heating (440
kHz) generator.
To estimate joint strength, the shear strength of bimetallic
specimens was determined by a special device. A minimum of three tests
were carried out for every experiment to ensure the confidence interval
of 15% with the probability factor of 95%.
The distribution of chemical elements in the bonding zone was
examined by the electron probe X-ray microanalysis (EPMA) and fracture
surfaces were studied by SEM (Zeiss EVO MA-15). Roughness of the
surfaces of mechanically metallized cermets was described using the
authentic mean values ([R.sub.a], [R.sub.z],) and maximum roughness
([R.sub.max]). A laser-based profilograph of the Mahr company was used.
The roughness measurements of the specimens were carried out in two
perpendicular directions.
[FIGURE 1 OMITTED]
3. RESULTS AND DISCUSSION
3.1. Characterization of the coatings
The mean results of mechanically metallized surface roughness
measurements of [Cr.sub.3][C.sub.2]- and TiC-based cermets are given in
Table 3 and SEM photographs of metallized surfaces are presented in Fig.
2.
The results in Table 3 show that after mechanical metallization the
surface roughness was increased, particularly the parameters [R.sub.z]
and [R.sub.max]. In the process of mechanical metallization, spreading
of Ti on the tops of surface asperities and a non-uniform distribution
of Ti were revealed (Fig. 2). The distribution of the surface roughness
was not uniform in the radial direction of the specimens.
[FIGURE 2 OMITTED]
3.2. Shear strength of joints
3.2.1. Chromium carbide based cermets
The shear strength of chromium carbide based cermets, brazed in
vacuum with AFM joints, is given in Fig. 3a. The maximum strength of 350
MPa is achieved with amorphous Ti-based composition S1201. Lower
strength was observed, when the brazing process was carried out in
vacuum and Ni-based amorphous filler metal grade S1311 was used.
Fracture of the joints occurred in the central part of brazed joints,
which confirms a good wettability of the cermet. Results of testing a
cermet, containing 10% and 30% Ni-binder, indicate that an increase in
the nickel content in the cermet results in the increase of the shear
strength of vacuum brazed joints, confirming the dominating role of the
binder phase content of the cermet to the mechanical properties of
joints. Results also demonstrated a significant influence of the brazing
atmosphere on the strength of brazed joints when amorphous filler metals
were used. In the case of air brazing (Fig. 3b), with an amorphous
Ti-based filler metal, shear strength was about half as high as that of
the brazed one in relatively low vacuum. Oxidation of the cermet surface
in fracture surfaces was observed.
Brazing with traditional filler metals in air (Fig. 3b) showed that
brazing with Ag-based traditional filler metals provides minimal
satisfactory results for the production of wear resistant parts (75
MPa). Air-brazed joints with Cu-based filler metal (grade F-Bronze) have
very low strength. Electrochemical deposition of a Ni coating to the
cermet surface was found to improve wetting of the cermets and an
increase of the shear strength of the joints up to 205 MPa, using
Ag-based filler metal. Silver coating on the cermet surface improved the
shear strength of the joints significantly when a Cu-based filler metal
was used. Mechanically deposited Ti coating was found to have negative
influence on the strength of brazed joints, as only 40 MPa shear
strength was achieved. Our experiments showed, that chromium carbide
based cermets can be successfully brazed to stainless steel by use of
Ag-based (grade Argo-Braze 49H) and also Cu-based (F-Bronze) traditional
filler metals and practically the same level (140 MPa) of shear strength
can be obtained when optimal fluxes are used.
[FIGURE 3 OMITTED]
3.2.2. Titanium carbide based cermets
Figure 4 a shows the shear strength of TiC60/FeNi cermet, brazed in
vacuum using different amorphous filler metals. The shear strength of
air brazed TiC50/NiMo cermet and WC-Co hardmetal as reference material
is shown in Fig. 4b.
Maximum strength of the brazed joints is provided by brazing in
vacuum. The most prospective amorphous filler metals for joining
TiC-based cermets are of the Cu-Ti type (grade S1204) and the Ni-Co-Fe
type (grade S1311), which gave the shear strength up to 260-300 MPa. The
chemical composition of amorphous filler metal grade S1204 is more
compatible with the basic component (TiC) of a cermet, and the grade
S1311--with the binder phase. A small decrease in the shear strength of
brazements was observed when the joining process with amorphous filler
S1311 was carried out in the air (Fig. 4b). It can be pointed out that
the shear strength of "TiC-cermet + steel" joints, brazed in
vacuum with amorphous filler metals (Fig. 4a), is comparable to that of
"hardmetal + steel" joints, brazed in air with traditional
filler metals (Fig. 4b).
[FIGURE 4 OMITTED]
For brazing TiC-based cermet in the air atmosphere, an Ag-Cu based
traditional filler metal with optimal fluxes should be used and the
shear strength up to 190 MPa can be achieved (Fig. 4b). Such strength is
sufficient in many applications.
The influence of electrochemical coatings on the strength of brazed
joints was contradictory. Nickel coating with the combination of
Ag-based filler metal showed a small improvement in the strength of air
brazed joints (Fig. 4b). Ag-coated cermets, brazed with Cu-based
traditional filler metal, showed low strength (40 MPa). No positive
effect of Ti coating (mechanical metallization) on the strength was
revealed when traditional Ag-Cu filler metal (grade LAg72) was used
(Fig. 4a) and the process was carried out in vacuum.
For the production of cutting and metalforming tools, working in
heavy service conditions, the first choice for TiC-based cermets are
Cu-Ti- and Ni-based amorphous filler metals grades S1204 and S1311,
respectively. For the production of bimetallic structural parts, the
F-Bronze and Argo 49 traditional filler metals can also be used. A lower
brazing temperature of the Ag-based filler metal (compared to the
Cu-based one) reduces the magnitude of internal stresses in the brazed
joints and this filler metal is expected to be favourable, when
reliability of joints is of importance.
3.3. Microstructure and fractographical analysis
Figure 5 shows the microstructure and element line-scans of vacuum
brazed joints "[Cr.sub.3][C.sub.2]-cermet + steel" (a) and
"TiC-cermet + steel" (b) using Ni-based amorphous filler metal
grade S1311. In the case of "TiC-cermet + steel" (Fig. 5b) a
smooth diffusion penetration of Ni from the molten filler to the cermet
and steel interface and an intensive iron diffusion from the steel to
filler metal can be observed. According to the fractographical analysis,
the joint fractured during testing usually in the zone close to the
filler metal-cermet interface. TiC particles float from the cermet into
the brazing zone (Fig. 5b).
In the case of joints "[Cr.sub.3][C.sub.2] + steel" (Fig.
5a) intensive diffusion of nickel to cermet-steel interface and steel
counterpart can be observed. In contrast to brazing of TiC-based cermets
(Fig. 5b) smooth diffusion of iron to cermet is observed. The weakest
area of joints is the diffusion zone close to the cermet in central area
of the joint.
Fractographical SEM examinations proved that the strength maximum,
as usual, corresponds to cases when the fracture occurs close to the
filler metal central zone. Lower strength of joints, brazed in the air
atmosphere, is connected with the fracture of joints at the interface
"cermet-filler metal". It indicates that wetting of carbides
in the cermets and diffusion between the contacting surfaces of the
carbide composite-filler metal was insufficient.
[FIGURE 5 OMITTED]
It should be mentioned that fast induction heating could cause
inhomogeneous heating of steel and cermet parts. During induction
heating the temperature in the pheripherical parts of specimens is
higher than in the central part. In some cases of air brazing even black
discoloration rings with a diameter of 2-3 mm were observed, indicating
extensive oxidation of this area. As in the central area of specimens
the temperature is the lowest, not all the filler metal is molten,
wetting of the surfaces is insufficient and therefore pores and flux
inclusions are not fully removed.
4. CONCLUSIONS
4.1. [Cr.sub.3][C.sub.2]-cermets
* The highest strength of the joints is achieved using the Ti-based
brazing amorphous filler metal (grade S1201). Vacuum brazing is
preferable to air brazing.
* The higher the binder content in the cermet, the higher shear
strength of the joints can be achieved.
* Air brazing with traditional Ag- and Cu-based filler metals gives
best results when metallization of the cermet with Ag and Ni is carried
out before brazing.
* Air brazing with Cu-based Cu-Zn filler metal and Ag-based Ag-Cu
filler metal enable to achieve satisfactory results only in brazing of
"[Cr.sub.3][C.sub.2]-cermet + stainless steel" joints.
4.2. TiC-based cermets
* The strength of joints "TiC-based cermet + steel" in
conditions of vacuum brazing is comparable to that of "WC-based
hardmetal + steel" joints when using amorphous filler metals
(grades S1204, S1311).
* TiC-based cermets can be brazed with good results in air using
traditional Cu- and Ag-based filler metals and the shear strength of
joints up to 200 MPa can be achieved.
* Preliminary metallization with Ti and Ag does not increase the
strength of the joints "TiC-based cermet + steel".
doi: 10.3176/eng.2012.3.08
ACKNOWLEDGEMENTS
This research was supported by the targeted project of the Estonian
Ministry of Education and Research (SF project No. 0140062s08) and
Estonian Science Foundation (grants Nos 6163 and 7889). The autors wish
to thank Dr. Eng J. Remmel from Julich Research Centre for his
contribution in metallization of the specimens and PhD J. Pirso from TUT
for help with production of the specimens.
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Andres Laansoo (a), Jakob Kubarsepp (a), Vello Vainola (b) and Mart
Viljus (c)
(a) Department of Materials Engineering, Tallinn University of
Technology, Ehitajate tee 5, 19086 Tallinn, Estonia;
andres.laansoo@ttu.ee
(b) Faculty of Mechanical Engineering, Tallinn University of
Applied Sciences, Parnu mnt. 62, 10135 Tallinn, Estonia
(c) Centre for Materials Research, Tallinn University of
Technology, Ehitajate tee 5, 19086 Tallinn, Estonia
Received 15 May 2012, in revised form 25 July 2012
Table 1. Chemical composition and properties of the cermets
Grade Carbide Binder Density,
content, composition, g/[cm.sup.3]
wt% wt%
HA15 WC, 85 15%Co 13.9
TiC50/NiMo TiC, 50 Ni + 20%Mo 6.4
TiC60/FeNi TiC, 60 Fe + 8%Ni 6.6
martensitic
steel
CrNi10 [Cr.sub.3] Ni 90 6.8
[C.sub.2], 90
CrNi30 [Cr.sub.3] Ni 70 7.2
[C.sub.2], 70
Grade Hardness, Transverse Oxidation
HRA rupture rate *, mg/
strength [cm.sup.2]
[R.sub.TZ],
MPa
HA15 87 2800 20
TiC50/NiMo 87 2300 0.25
TiC60/FeNi 88 2200 -
CrNi10 91 750 0.04
CrNi30 86 1200 0.08
* Weight gain rate at 800 [degrees]C, 2 hours.
Table 2. Chemical composition of filler metals,
Brazing conditions and temperatures
Grade Type Composition
S1201 AFM 52Ti-24Cu-12Zr-12Ni
S1204 AFM 28Ti-72 Cu
S1311 AFM 70Ni-16Co-5Fe-4Si-4B-0.4Cr
MBF20 AFM 82Ni-7Cr-4Si-3B-3Fe
Argo-Braze FM 49Ag-16Cu-23 Zn-7.5Mn-4.5Ni
49H
LAg72 FM 72Ag-28Cu
F-Bronze FM 57.5Cu-38.5Zn-2Mn-2Co
Grade Brazing Brazing
conditions temperature,
[degrees]C
S1201 Vacuum 900
S1204 Vacuum 900
S1311 Vacuum, air 1020
MBF20 Vacuum 1070
Argo-Braze Air 750
49H
LAg72 Vacuum 830
F-Bronze Air 980
Table 3. Characteristics of mechanically metallized
surfaces
Parameter, Before After metallization
[micro]m metallization
Average In the
centre of
the sample
[R.sub.a] 0.65 1.06-1.28 1.40
[R.sub.z] 6.67 10.4-13.4 13.5
[R.sub.max] 7.15 12.2-13.2 21.6
