EP0874063A1 - Cemented carbide, coated articles having the cemented carbide as base, in particular coated hard tools - Google Patents
Cemented carbide, coated articles having the cemented carbide as base, in particular coated hard tools Download PDFInfo
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- EP0874063A1 EP0874063A1 EP98303258A EP98303258A EP0874063A1 EP 0874063 A1 EP0874063 A1 EP 0874063A1 EP 98303258 A EP98303258 A EP 98303258A EP 98303258 A EP98303258 A EP 98303258A EP 0874063 A1 EP0874063 A1 EP 0874063A1
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- Prior art keywords
- cemented carbide
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- set forth
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- surface layer
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
- C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Definitions
- Samples No. 4 to 14 having composition shown in Table 4 were prepared. Samples No. 12 to 14 were comparative examples.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Abstract
Novel cemented carbide having improved hardness and corrosion
resistance comprising 3 to 25 % by weight of the sum of Co and Ni, 10 to
30 % by weight of chromium in the term of chromium carbide with
respect to the sum of Co and Ni and the balance being tungsten carbide
and inevitable impurities. The cemented carbide is advantageously used
in cutting tools for hard-to-cut materials and in various fields which
require improved hardness and corrosion resistance such as structural
parts, machine parts and ornaments. On a base made of the cemented
carbide, the cutting tool has a surface layer including at least one layer
made of at least one compound selected from a group comprising nitrides,
carbides, carbonitrides and oxides of at least one element selected from a
group comprising IVa elements, Va elements, Al, B and Si.
Description
The present invention relates to a novel cemented carbide and
coated cemented carbide having the cemented carbide as a base, and
coated hard tools prepared therefrom.
The cemented carbide and coated cemented carbide according to the
invention are advantageously used to prepare machining tools having
improved hardness and corrosion resistance, and can be used in a variety
applications which require improved hardness and corrosion resistance
such as structural parts, machine parts and ornaments or decorations.
The coated hard tools having a base of the cemented carbide
according to the present invention show very high resistance to wear
welding and can be used in cutting work in such materials that are
difficult to be cut.
Improvement in hardness and strength are uninterruptedly
requested in cemented carbide for machining tools, since materials to be
worked become harder and cutting speed become faster.
For example, in cutting tools, cemented carbide is required to resist
so-called interface-wear caused by contact with a surface (so called black
skin) of material to be cut, in addition to resistance to flank-wear. High
resistance to crater-wear which is often observed at a cutting face is also
required. Recently, resistance to welding of material to be cut onto
cutting tools is also required. Such welding is often observed in cutting
of materials that are difficult to be cut (hereinafter, hard-to-cut materials)
such as Ni alloy, Ti alloy and steels of high hardness and forms a build-up
edge which causes chipping of tools, resulting in shortening of tool life.
JP-A-61-12847 discloses to add V (vanadium) and Cr (chromium)
to limit growth of grains of WC (tungsten carbide) so as to improve the
corrosion resistance.
JP-A-4-31012 and "Powders and powder metallurgy" 31, 1984, p56
describes such a fact that addition of Cr3C2 (chromium carbide) improve
the corrosion resistance.
In practice, in cemented carbide for cutting tools, fine particles of
WC is used to improve the hardness and Cr3C2 is added to limit growth of
grains and to resist interface-wear and crater-wear so as to improve the
corrosion resistance.
However, decrement in resistance to propagation of crack is often
observed in cemented carbide produced with fine particles. In fact,
greater energy is necessary to propagation crack in the coarse particles
and hence the coarse particles contribute to resist to propagation of crack.
Still more, fine particles are easily fall off than coarse particles
because gripping force of hard particles in bonding phase of cemented
carbide used as cutting tool is lost or lowered at high cutting
temperatures, resulting in rapid abrasion wearing.
In this type cemented carbide, higher content of inevitable
impurities cause formation of fragile phase in alloy when Cr3C2 is added,
resulting in that the resistance to crack propagation is lost and hence the
strength is lost.
On the other hand, attempt has been made to deposit a surface layer
such as TiN on a surface of cemented carbide to improve its wear
resistance. However, the base material of cemented carbide suffers from
severe wear so that satisfactory effect or advantage is not yet obtained.
An object of the present invention is to solve the above-mentioned
problems and to provide a novel cemented carbide possessing desired
characteristics for cutting tools and improved in wear resistance.
Another object of the present invention is to provide a coated
cemented carbide comprising the cemented carbide as a base and a surface
layer and possessing high resistance to corrosion and welding, which is
advantageously used in hard cutting tools for hard-to-cut materials.
The present invention provides a cemented carbide comprising 3 to
25 % by weight of the sum of Co and Ni, 10 to 30 % by weight of
chromium in the term of chromium carbide (Cr3C2 ) with respect to the
sum of Co and Ni and the balance being tungsten carbide (WC) and
inevitable impurities.
The present invention also provide a coated cemented carbide, in
particular coated hard tool, comprising a base of the cemented carbide
and a surface layer deposited on the base, the surface layer including at
least one layer made of at least one compound selected from a group
comprising nitrides, carbides, carbonitrides and oxides of at least one
element selected from a group comprising IVa elements, Va elements, Al,
B and Si.
In a preferred embodiment of cemented carbide according to the
present invention, a proportion of Ni ranges from 0.4 to 80 % by weight
to the sum of Co and Ni.
In another preferred embodiment of cemented carbide according to
the present invention, an average particle size of tungsten carbide ranges
from 0.3 to 5 µm.
In still another preferred embodiment of cemented carbide
according to the present invention, tungsten carbide is composed of fine
particles having an average particle size of 0.3 to 1.1 µm and coarse
particles having an average particle size of 1.2 to 5 µm, and the ratio of
said coarse particles to the total amount of said tungsten carbide being 0.1
to 0.9.
The cemented carbide according to the present invention is
characterized in increased proportion of Cr3C2 (chromium carbide)
comparing to the conventional cemented carbides.
In fact, the cemented carbide according to the present invention
comprising 3 to 25 % by weight of Co + Ni, 10 to 30 % by weight of
chromium in the term of chromium carbide (Cr3C2 ) with respect to the
sum of Co and Ni and the balance being tungsten carbide (WC) and
inevitable impurities, assure extremely longer life time in cutting tools
comparing to known types cemented carbides such as WC/Co, WC/trace
of Cr3C2-Co and WC/trace of Cr3C2/Co/trace of Ni type in cutting of Ni
alloys such as inconel and nimonic.
This characteristic is far more improved when the cemented
carbide contains 0.4 to 80 % by weight of Ni to the sum of Co and Ni.
Chromium can be introduced in a form of chromium carbide or of
elemental metal chromium or other chromium compound as far as the
proportion of chromium expressed in term of chromium carbide falls in
the defined range.
If the contents of Co and Ni is not higher than 3 % by weight, the
toughness is undesirably lowers. On the other hand, if the contents of Co
and Ni exceeds 25 % by weight, the resistance to plastic deformation and
wearing become disadvantageously low. Therefore, the contents of Co
and Ni should be in the range of 3 to 25 % by weight.
If a proportion of chromium in term of chromium carbide (Cr3C2)
with respect to the amount of Co and Ni is not higher than 10 % by
weight, resistance to oxidation and interface-wearing become poor. On
the other hand, if it exceeds 30 % by weight, fragile phase is generated
resulting in sharp drop in toughness. Therefore, the weight ratio of
Cr3C2 to the sum of Co and Ni is preferably in a range of 10 to 30 % by
weight.
If the proportion of Ni is not higher than 0.4 % by weight to the
sum of Co and Ni, desired resistance to wearing and interface wearing
can not be obtained. On the other hand, if the proportion of Ni exceeds
80 % by weight, sintering become insufficient resulting in lowering of
toughness or sintering must be effected at higher temperature which
deteriorate wearing resistance.
If the average particle size of tungsten carbide is not higher than
0.3 µm, sufficient sintering can not be effected and hence the strength
become poor. If the average particle size becomes larger than 5 µm,
wearing resistance become insufficient.
If the ratio of course particles to the total amount of tungsten
carbide is not higher than 0.1, the strength become insufficient and if it
exceeds 0.9, the wear-resistance becomes insufficient.
The coated hard tool according to the present invention comprises a
base made of the cemented carbide according to the present invention and
a surface layer deposited on a surface of the cemented carbide base. The
surface layer includes at least one layer made of at least one compound
selected from a group comprising nitrides, carbides, carbonitrides and
oxides of at least one element selected from a group comprising IVa
elements, Va elements, Al, B and Si.
The coated hard tools having the surface layer possess very longer
tool life comparing to known coated hard tools produced by the
conventional technique.
In the preferred embodiment of the coated hard tool according to
the present invention, the surface layer includes a multi-layered structure
consisting of at least two unit layers superimposed alternately, each unit
layer being made of at least one compound selected from a group
comprising nitrides, carbides, carbonitrides and oxides of at least one
element selected from a group comprising IVa elements, Va elements, Al,
B and Si, each unit layer having a thickness of 0.2 to 100 nm, and the
multi-layered structure having a total thickness of 0.5 to 10 µm.
If the thickness of each unit layer is not higher than 0.2 nm,
adjacent layers are intermixed each other and hence advantages of the
multi-layered structure can not be obtained. Similarly, if the thickness of
each unit layer exceeds 100 nm, interaction of adjacent unit layers can not
be expected so that advantage of the multi-layered structure is not
obtained.
Advantages of coating are not obtained if the total thickness of the
multi-layered structure is not higher than 0.5 µm. On the other hand, if
the total thickness exceeds 10 µm, chipping increases disadvantageously.
Addition of at least one element selected from a group comprising
Ge, Sn and Pb to at least one unit layer makes tool life longer.
In another embodiment of the coated hard tools according to the
present invention, the surface layer comprises the multi-layered structure
and mono-layer structure having no layered structure, two structures
being superimposed alternately at least for five (5) times, said mono-layer
structure being made of at least one compound selected from a group
comprising nitrides, carbides, carbonitrides and oxides comprising at least
one element selected from a group comprising IVa elements, Va elements,
Al, B and Si and having a thickness of 100 to 5000 nm, and the surface
layer having a total thickness of 0.5 to 10 µm.
Thanks to this structure, stress in the coated surface layer decrease
and chipping of the coated surface layer decrease, which assure very long
tool life. In this embodiment, advantage of stress relaxation can not be
expected if the multi-layered structure and mono-layer structure are not
superimposed alternately for more than 5 times (more than 10
structures).
The coated hard tool according to the invention has preferably a
bottom layer consisting of TiN and having a thickness of 0.02 to 2 µm. If
this bottom layer has not a thickness higher than 0.2 µm, no effect as
coating layer is obtained. On the contrary, if the thickness exceed 2 µm,
wear-resistance is spoiled disadvantageously.
The coated hard tool according to the invention has preferably an
outermost layer having a surface roughness "Ra" in accordance with JIS B
0601 is 0.18 µm. This permits tips to flow smoothly and prevent welding
of chip so that a work to be cut can be maintained in very good condition
on its surface and cutting edge chipping and breaking from the welded
portions can be prevented advantageously, resulting in longer tool life. If
the surface roughness "Ra" exceed 0.18 µm, trouble of welding increase.
Now, the present invention will be explained with reference to
Examples. The following disclosure is merely for explanation of the
present invention but no way limits the scope of the present invention.
Following components were mixed in a wet form to prepare
material powder No. 1:
% by weight | |
WC powder having average particle size of 2 µm: | 28 |
WC powder having average particle size of 0.7 µm: | 65.7 |
Cr3C2 powder having average particle size of 2 µm | 0.8 |
Ni powder having average particle size of 1.5 µm | 0.5 |
Co powder having average particle size of 1.5 µm | 5 |
The material power No. 1 thus prepared was compacted and then
sintered in vacuum under 10-2 Torr at a temperature of 1400 °C to obtain
sample No. 1. In this sample No. 1, a proportion of Cr3C2 to the sum of
Co and Ni is 14.5 % by weight, a proportion of Ni to the sum of Co and
Ni is 9.1 % by weight. An average particle size of total WC is 1 µm and
a ratio of coarse WC powder having average particle size of 2 µm to the
total WC is 0.3.
Following components were mixed in a wet form to prepare
material powder No. 2.
% by weight | |
WC powder having average particle size of 1 µm: | 89 |
Cr3C2 powder having average particle size of 2 µm | 2 |
Ni powder having average particle size of 1.5 µm | 3 |
Co powder having average particle size of 1.5 µm | 6 |
The material power No. 2 thus prepared was compacted and then
sintered in vacuum under 10-2 Torr at a temperature of 1,400 °C to obtain
sample No. 2. In this sample No. 2, a proportion of Cr3C2 to the sum of
Co and Ni is 22.2 % by weight, a proportion of Ni to the sum of Co and
Ni is 33.3 % by weight.
For comparison, material powder No. 3 whose composition is
outside the present invention was also prepared. The material powder
No. 3 was prepared from the same formulation as sample No. 1 but the
content of Cr3C2 powder was changed to 0.3 % by weight and the content
of Co powder was changed to 5.5 % by weight.
The material powder No. 3 was compacted and sintered under the
same conditions as sample No. 1 to obtain sample No. 3. In this sample
No. 3, a proportion of Cr3C2 to the sum of Co and Ni is 5 % by weight
and a proportion of Ni to the sum of Co and Ni is 8.3 % by weight.
Table 1 shows the results of mechanical properties and corrosion
resistance of samples No. 1 to 3.
In Table 1, corrosion loss was determined after samples were
placed in 36 % HCl solution at 50 °C for 8 hours. Oxidation gain was
determined after the samples were left in atmospheric environment at
1,000 °C for 30 minutes.
Hardness (Hv) | Deflective strength (kg/mm2) | Corrosion loss (g/m2·hr) | Oxdation gain (mg/mm2·hr) | |
Sample 1 | 1820 | 235 | 2.13 | 0.02 |
Sample 2 | 1730 | 210 | 1.97 | 0.01 |
Sample 3 | 1780 | 285 | 10.5 | 1.57 |
Table 1 reveals such facts that the samples No. 1 and 2 according to
the present invention possess slightly lower deflective strength due to
higher Cr3C2 contents but highly improved corrosion loss and oxidation
gain comparing to sample No. 3 of comparative example.
In the present invention, sample No. 2 having higher content of
Cr3C2 shows better corrosion resistance than sample No. 1.
Cutting tools were manufactured from the samples No. 1 to 3
prepared in Example 1. The performances of tools were evaluated by
actual cutting work effected under the conditions shown in Table 2.
Cutting condition 1 | Cutting condition 2 | Cutting condition 3 | |
Shape of tool | CNMG432 | CNMG432 | CNMG432 |
Material to be cut | SUS304 round rod | SCM435 (Hs=250) round rod having longitudinal four grooves | Incone 1718 round rod |
Cutting speed | 120 m/min. | 200 m/min. | 50 m/min. |
Feed | 0.2 mm/revolution | 0.28 mm/revolution | 0.2 mm/revolution |
Depth | 1.5 mm | 1.0 mm | 1.5 mm |
Cutting oil | water soluble | - | water soluble |
Cutting time | 15 minutes | 5 minutes | 20 minutes |
Evaluation | Maximum width of wear (mm) | Number of broken cutting edges out of 20 | Average width of wear (mm) |
Performance of tools was evaluated by the maximum width of wear
in the condition 1, by the number of broken cutting edges out of 20
cutting edges in the condition 2 and by the average width of wear in the
condition 3 respectively. The result are summarized in Table 3.
Sample No. | Note | Cutting condition 1 | Cutting condition 2 | Cutting condition 3 |
1 | Example | 0.08 | 4 | 0.12 |
2 | Example | 0.25 | 7 | 0.26 |
3 | Comparative Example | 1.24 | 20 | more than 1 mm in 10 min. |
Table 3 reveals that cutting tools made from cemented carbide
according to the present invention possess very high performances in the
resistance to wear and breakage.
Sample No. 1 shows better characteristics than sample No. 2 in
cutting properties.
Samples No. 4 to 14 having composition shown in Table 4 were
prepared. Samples No. 12 to 14 were comparative examples.
Table 5 summarizes the results of characteristics of samples tested.
In this table, oxidation gain was evaluated by the same method as
Example 1 and cutting condition 3 was the same as Example 2.
Sample No. | Hardness (Hv) | Deflective strength (kg/mm2) | Oxidation gain | Cutting condition 3 |
4 | 1580 | 270 | 0.02 | 0.17 |
5 | 1840 | 210 | 0.02 | 0.38 |
6 | 1510 | 255 | 0.01 | 0.56 |
7 | 1670 | 240 | 0.02 | 0.24 |
8 | 1490 | 220 | 0.01 | 0.41 |
9 | 1600 | 270 | 0.02 | 0.37 |
10 | 1280 | 305 | 0.01 | 0.87 |
11 | 1360 | 280 | 0.02 | 0.74 |
12 | 1760 | 145 | 0.01 | 1 |
13 | 1510 | 210 | 9.44 | 2 |
14 | 1300 | 290 | 11.44 | 3 |
Coated hard tools were manufactured by depositing following
coatings A to N on cemented carbides of Examples 1 to 3 and then
performance of the tools thus obtained were evaluated.
- A :
- sample coated with 2 µm of ZrN
- B :
- sample coated with 10 µm of HfN
- C :
- sample coated with 8 µm of VCN
- D :
- sample coated with 10 µm of TiAIN
- E :
- sample coated with 2 µm of BN
- F :
- sample coated with 5 µm of Al2O3 containing 1 % Si
- G :
- sample coated with a surface layer having the total thickness of 3.5 µm and comprising 2,500 TiN layers each having a thickness of 0.2 nm and 2,500 AIN layers each having a thickness of 0.5 nm superimposed alternately.
- H=
- sample coated with a surface layer having the total thickness of 3.5 µm and comprising 250 TiN layers each having a thickness of 2 nm and 250 AIN layers each having a thickness of 5 nm superimposed alternately.
- I=
- sample coated with a surface layer having the total thickness of 9 µm and comprising 25 Al2O3 layers each having a thickness of 80 nm and 25 HfC layers each having a thickness of 100 nm superimposed alternately.
- J=
- sample coated with a surface layer having the total thickness of 3.5 µm and comprising 250 TiN layers each having a thickness of 2 nm and 250 AIN (containing 1% Si) layers each having a thickness of 5 nm superimposed alternately.
- K=
- sample coated with a surface layer having the total thickness of 2.05 µm and comprising five layers of multi-layer structure and five layers of mono-layer structure, the multi-layer structure comprising 15 TiN layers each having a thickness of 2 nm and 15 AlN4 layers each having a thickness of 5 nm while the mono-layer structure is made of TiCN layer having a thickness of 0.2 µm.
- L=
- sample coated with a surface layer having the total thickness of 3.52 µm and comprising a TiN layer of 0.02 µm thickness at an interface with a base material and a layer of multi-layer structure comprising 250 TiN layers each having a thickness of 2 nm and 250 AIN layers each having a thickness of 5 nm superimposed alternately.
- M=
- sample coated with a surface layer having the total thickness of 3.51 µm and comprising a TiN layer of 0.01 µm thickness at an interface with a base material and a layer of multi-layer structure comprising 250 TiN layers each having a thickness of 2 nm and 250 AIN layers each having a thickness of 5 nm superimposed alternately.
- N=
- sample coated with a surface layer having the total thickness of 14.5 µm and comprising a TiN layer of 11 µm thickness at an interface with a base material and a layer of multi-layer structure comprising 250 TiN layers each having a thickness of 2 nm and 250 AIN layers each having a thickness of 5 nm superimposed alternately.
Cutting performance of samples were evaluated under the condition
3 of Example 2.
Table 6 to Table 8 summarize structures of surface layers used.
Table 9 is a list showing relation between sample numbers and the
surface layer and base material sample Nos.
Table 10 shows the results obtained.
Surface layer list (1) | |||
Surface layer No. | Component | Thickness (µm) | Doped Element |
A | ZrN | 2 | |
B | HfN | 10 | |
C | VCN | 8 | |
D | TiAIN | 10 | |
E | BN | 2 | |
F | Al2O3 | 5 | Si 1% |
Surface layer list (3) | ||||
Surface layer | Multi-layer structure | TiN layer at Interface thickness (µm) | ||
Unit layer 1 (thickness µm) | Unit layer 2 (thickness µm) | Number of layers | ||
L | TiN (2) | AIN (5) | 500 | 0.02 |
M | TiN (2) | AIN (5) | 500 | 0.01 |
N | Al2O3 ( 2) | HfC ( 5) | 500 | 11 |
List of sample No. | |||
Surface layer | Base material sample No. | ||
1 | 2 | 3 | |
A | A-1 | A-2 | A-3 |
B | B-1 | B-2 | B-3 |
C | C-1 | C-2 | C-3 |
D | D-1 | D-2 | D-3 |
E | E-1 | E-2 | E-3 |
F | F-1 | F-2 | F-3 |
G | G-1 | G-2 | G-3 |
H | H-1 | H-2 | H-3 |
I | I-1 | I-2 | I-3 |
J | J-1 | J-2 | J-3 |
K | K-1 | K-2 | K-3 |
L | L-1 | L-2 | L-3 |
M | M-1 | M-2 | M-3 |
N | N-1 | N-2 | N-3 |
Surface layer | Sample No. | Wear4 | Sample No. | Wear4 | Sample No. | Wear4 |
A | A-1 | 0.069 | A-2 | 0.169 | A-3 | more than 1 mm in 10 min. |
B | B-1 | 0.072 | B-2 | 0.173 | B-3 | more than 1 mm in 10 min. |
C | C-1 | 0.076 | C-2 | 0.188 | C-3 | more than 1 mm in 10 min. |
D | D-1 | 0.068 | D-2 | 0.17 | D-3 | more than 1 mm in 10 min. |
E | E-1 | 0.078 | E-2 | 0.175 | E-3 | more than 1 mm in 10 min. |
F | F-1 | 0.075 | F-2 | 0.174 | F-3 | more than 1 mm in 10 min. |
G | G-1 | 0.049 | G-2 | 0.148 | G-3 | more than 1 mm in 10 min. |
H | H-1 | 0.045 | H-2 | 0.145 | H-3 | more than 1 mm in 10 min. |
I | I-1 | 0.055 | I-2 | 0.15 | I-3 | more than 1 mm in 10 min. |
J | J-1 | 0.039 | J-2 | 0.136 | J-3 | more than 1 mm in 10 min. |
K | K-1 | 0.033 | K-2 | 0.126 | K-3 | more than 1 mm in 15 min. |
L | L-1 | 0.042 | L-2 | 0.138 | L-3 | more than 1 mm in 12 min. |
M1 | M-1 | 0.12 | M-2 | 0.26 | M-3 | more than 1 mm in 10 min. |
N2 | N-1 | 0.01 | N-2 | 0.24 | N-3 | more than 1 mm in 10 min. |
Control3 | 1 | 0.12 | 2 | 0.26 | 3 | more than 1 mm in 10 min. |
M1 : M-1, M-2 are outside the scope of invention | ||||||
N2 : N-1, N-2 are outside the scope of invention | ||||||
Control3: sample having no surface layer | ||||||
Wear4: mm |
In order to validate the effect of surface roughness, the sample No.
1 of Example 1 was coated with a variety of TiAIN layers each having a
surface roughness (Ra) shown in Table 11 and the same cutting test as
Example 4 was effected. The results are shown in Table 11.
Sample No. | Ra (mm) | wea (mm) | welding |
5-1 | 0.10 | 0.068 | no deposition |
5-2 | 0.19 | 0.090 | observed |
5-3 | 0.25 | 1.200 | severe welding |
This result shows that risk of welding is reduced when the surface
roughness become smaller, so that better cutting performance is obtained.
As explained above, the cemented carbide according to the present
invention possess excellent corrosion resistance. Therefore, its use is not
limited to cutting tools but it can be used, as highly reliable cemented
carbide material, in a variety of applications where good corrosion
resistance is required, in particular in the field of cutting work of hard-to-cut
materials such as high hardness steel, Ni based alloy, Co based alloy
and Ti based alloy for hot rolling rolls, watch frames, sleeves and
mechanical seal for sea water pump, high pressure valve seat and ball
which require high corrosion resistance and hard ornaments or
decorations.
Claims (16)
- Cemented carbide comprising 3 to 25 % by weight of the sum of Co and Ni, 10 to 30 % by weight of chromium in the term of chromium carbide with respect to the sum of Co and Ni and the balance being tungsten carbide and inevitable impurities.
- The cemented carbide set forth in claim 1 wherein a proportion of Ni is 0.4 to 80 % by weight to the sum of Co and Ni.
- The cemented carbide set forth in claim 1 or 2 wherein an average particle size of said tungsten carbide is 0.3 to 5 µm.
- The cemented carbide set forth in any one of claims 1 to 3 wherein said tungsten carbide is composed of fine particles having an average particle size of 0.3 to 1.1 µm and coarse particles having an average particle size of 1.2 to 5 µm, and the ratio of said coarse particles to the total amount of said tungsten carbide being 0.1 to 0.9.
- A coated cemented carbide comprising a base of said cemented carbide set forth in any one of claim 1 to 4 and a surface layer deposited on said base.
- The coated cemented carbide set forth in claim 5 wherein said surface layer includes at least one layer made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides of at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si.
- The coated cemented carbide set forth in claim 5 or 6 wherein said surface layer includes a multi-layered structure consisting of at least two unit layers superimposed alternately, each unit layer being made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides of at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si, each unit layer having a thickness of 0.2 to 100 nm, and said multi-layered structure having a total thickness of 0.5 to 10 µm.
- The coated cemented carbide set forth in claim 7 wherein that at least one of unit layers contains at least one elements selected from a group comprising Ge, Sn and Pb.
- The coated cemented carbide set forth in claim 7 or 8 wherein said surface layer comprises said multi-layered structure and mono-layer structure having no layered structure, two structures being superimposed alternately at least for five times, said mono-layer structure being made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides comprising at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si and having a thickness of 100 to 5000 nm, and said surface layer having a total thickness of 0.5 to 10 µm.
- A coated hard tool comprising a base made of said cemented carbide set forth in any one of claims 1 to 4 and a surface layer deposited on a surface of said cemented carbide base, said surface layer including at least one layer made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides of at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si.
- The coated hard tool set forth in claim 10 wherein said surface layer includes a multi-layered structure consisting of at least two unit layers superimposed alternately, each unit layer being made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides of at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si, each unit layer having a thickness of 0.2 to 100 nm, and said multi-layered structure having a total thickness of 0.5 to 10 µm.
- The coated hard tool set forth in claim 11 wherein that at least one of unit layers contains at least one elements selected from a group comprising Ge, Sn and Pb.
- The coated hard tool set forth in claim 11 or 12 wherein said surface layer comprises said multi-layered structure and mono-layer structure having no layered structure, said multi-layered structure and said mono-layer structure being superimposed alternately at least for five times, said mono-layer structure being made of at least one compound selected from a group comprising nitrides, carbides, carbonitrides and oxides comprising at least one element selected from a group comprising IVa elements, Va elements, Al, B and Si and having a thickness of 100 to 5000 nm, and said surface layer having a total thickness of 0.5 to 10 µm.
- The coated hard tool set forth in any one of claims 10 to 13 wherein said surface layer includes a bottom layer made of TiN having a thickness of 0.02 to 2 µm.
- The coated hard tool set forth in any one of claims 10 to 14 wherein said surface layer has an outer most layer whose surface roughness Ra is smaller than 0.18 µm.
- Use of said coated cemented carbide set forth in any one of claim 5 to 9 in hard tools.
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP123321/97 | 1997-04-25 | ||
JP12332197 | 1997-04-25 | ||
JP10097297A JPH116025A (en) | 1997-04-25 | 1998-04-09 | Cemented carbide, and coated alloy and coated hard tool using this cemented carbide as base material |
JP97297/98 | 1998-04-09 |
Publications (1)
Publication Number | Publication Date |
---|---|
EP0874063A1 true EP0874063A1 (en) | 1998-10-28 |
Family
ID=26438480
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98303258A Ceased EP0874063A1 (en) | 1997-04-25 | 1998-04-27 | Cemented carbide, coated articles having the cemented carbide as base, in particular coated hard tools |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP0874063A1 (en) |
JP (1) | JPH116025A (en) |
IL (1) | IL124207A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114700656A (en) * | 2022-04-20 | 2022-07-05 | 广东省科学院中乌焊接研究所 | Preparation method of nickel-based flux-cored wire suitable for additive manufacturing |
EP1122226B2 (en) † | 1999-12-03 | 2022-10-26 | Sumitomo Electric Industries, Ltd. | Coated pcbn cutting tools |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2002146515A (en) * | 2000-11-14 | 2002-05-22 | Toshiba Tungaloy Co Ltd | Hard film superior in slidableness and its coating tool |
JP2002155336A (en) * | 2000-11-15 | 2002-05-31 | Fuji Dies Kk | Grooving roll for strip for manufacture of heat transfer tube |
JP2008138242A (en) * | 2006-11-30 | 2008-06-19 | General Electric Co <Ge> | Wear resistant coating, and article having the wear resistant coating |
JP6399349B2 (en) * | 2014-10-31 | 2018-10-03 | 三菱マテリアル株式会社 | Diamond coated cemented carbide cutting tool |
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JPS6112847A (en) * | 1984-06-26 | 1986-01-21 | Mitsubishi Metal Corp | Sintered hard alloy containing fine tungsten carbide particles |
EP0665308A1 (en) * | 1993-08-16 | 1995-08-02 | Sumitomo Electric Industries, Ltd. | Cemented carbide alloy for cutting tool and coated cemented carbide alloy |
JPH08319532A (en) * | 1995-05-19 | 1996-12-03 | Toshiba Tungaloy Co Ltd | Sintered hard alloy for punching tool |
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GB1434764A (en) * | 1973-06-04 | 1976-05-05 | Ici Ltd | Pesticidal phosphorus-containing pyrimidine derivative |
JPH0635638B2 (en) * | 1988-10-03 | 1994-05-11 | 東芝タンガロイ株式会社 | Cemented carbide for precision dies and coated cemented carbide for precision dies |
JP2623508B2 (en) * | 1989-10-30 | 1997-06-25 | 東芝タンガロイ株式会社 | Coated cemented carbide with adjusted surface roughness |
JP3127708B2 (en) * | 1994-03-11 | 2001-01-29 | 住友電気工業株式会社 | Coated cemented carbide for cutting tools |
JPH08337838A (en) * | 1995-06-09 | 1996-12-24 | Toshiba Tungaloy Co Ltd | Cemented carbide for metal plastic working tool |
JPH093585A (en) * | 1995-06-22 | 1997-01-07 | Toshiba Tungaloy Co Ltd | Cemented carbide for cutting hard roll material and coated cemented carbide |
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1998
- 1998-04-09 JP JP10097297A patent/JPH116025A/en active Pending
- 1998-04-23 IL IL12420798A patent/IL124207A/en not_active IP Right Cessation
- 1998-04-27 EP EP98303258A patent/EP0874063A1/en not_active Ceased
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JPS6112847A (en) * | 1984-06-26 | 1986-01-21 | Mitsubishi Metal Corp | Sintered hard alloy containing fine tungsten carbide particles |
EP0665308A1 (en) * | 1993-08-16 | 1995-08-02 | Sumitomo Electric Industries, Ltd. | Cemented carbide alloy for cutting tool and coated cemented carbide alloy |
JPH08319532A (en) * | 1995-05-19 | 1996-12-03 | Toshiba Tungaloy Co Ltd | Sintered hard alloy for punching tool |
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BANERJEE D ET AL: "Effect of binder-phase modification and Cr/sub 3/C/sub 2/ addition on properties of WC-10Co cemented carbide", JOURNAL OF MATERIALS ENGINEERING AND PERFORMANCE, OCT. 1995, USA, vol. 4, no. 5, ISSN 1059-9495, pages 563 - 572, XP000541466 * |
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1122226B2 (en) † | 1999-12-03 | 2022-10-26 | Sumitomo Electric Industries, Ltd. | Coated pcbn cutting tools |
CN114700656A (en) * | 2022-04-20 | 2022-07-05 | 广东省科学院中乌焊接研究所 | Preparation method of nickel-based flux-cored wire suitable for additive manufacturing |
CN114700656B (en) * | 2022-04-20 | 2024-04-02 | 广东省科学院中乌焊接研究所 | Preparation method of nickel-based flux-cored wire suitable for additive manufacturing |
Also Published As
Publication number | Publication date |
---|---|
IL124207A (en) | 2001-03-19 |
JPH116025A (en) | 1999-01-12 |
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