CN105861903B - Hard alloy - Google Patents
Hard alloy Download PDFInfo
- Publication number
- CN105861903B CN105861903B CN201610367856.1A CN201610367856A CN105861903B CN 105861903 B CN105861903 B CN 105861903B CN 201610367856 A CN201610367856 A CN 201610367856A CN 105861903 B CN105861903 B CN 105861903B
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- Prior art keywords
- hard alloy
- phase
- binder
- binder phases
- phases
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Classifications
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- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Powder Metallurgy (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
The invention discloses a kind of hard alloy, including hard phase and Co Binder Phases, Cr or/and Mo are wherein mainly contained in Co Binder Phases, and Ni is free of in Co Binder Phases.The hard alloy of the present invention uses the Co Binder Phases without Ni, by adding Cr and/or Mo elements in the Co Binder Phases without Ni, Co Binder Phases HCP switchs to the increase of FCC transformation temperatures, can preventing Co Binder Phases, HCP is transformed into volume expansion after FCC phase transformations and Co phase bleeds caused by softening when the temperature rises, to greatly improve the cutting ability and service life of hard alloy.
Description
Technical field
The present invention relates to a kind of hard alloy still at high temperature with preferable cutting ability and mechanical property.
Background technology
Hard alloy is to be with the carbide of high rigidity refractory metal (such as tungsten carbide wc, titanium carbide TiC) micron powder
Main component (is used as hard phase), with cobalt (Co) for Binder Phase, is aided with inhibition phase, is sintered in vacuum drying oven or hydrogen reducing furnace
Made of sintered metal product.And currently used for the cemented carbide material of the technical fields such as cutter, mold, mainly with WC or other
Carbide is as hard phase, and using Co as Binder Phase, for example main chemical compositions are WC-Co, WC-TiC-Co, WC-TiC-TaC-
The hard alloy etc. of Co formulas.As shown in Figure 1, Co Binder Phases are close-packed hexagonal knot when temperature is less than 430 DEG C in hard alloy
Structure (HCP structures), atomic arrangement is closer, and density is higher；When temperature is higher than 430 DEG C, for face-centred cubic structure, (FCC is tied
Structure), atomic arrangement is more open at this time, and density declines suddenly, and volume acutely expands (about 1.35%).So in machining mistake
Since Co Binder Phases when frictional heating is at 400 DEG C or more or under high temperature can be by the close-packed hexagonal structure (HCP under low temperature in journey
Phase) it is changed into face-centred cubic structure (FCC phases), it causes Binder Phase volume expansion, soften (test data is as shown in Figure 2), bond
Phase bleed (Co Binder Phase mechanism of running off schematic diagrames are as shown in Figure 3), and significantly reduce the cutting of hard alloy at high temperature
Performance and mechanical performance, and these features were in the 5th phases publication of volume 28 in 2007《Material heat treatment journal》In 105-
It was also reported in page 110 " researchs of hard alloy intensity variation with temperature and failure mechanism "；And how to improve Co Binder Phases
This transformation temperature, be to be related to hard alloy to answer more extensively to improve cutting ability under hard alloy high temperature and mechanical property
Problem.Researcher, which has focused largely on, at present is added the member such as Ni usually stable FCC configuration, in this way meeting in Co Binder Phase matrixes
Cause the transformation temperature reduction, although the hardness, cutting ability of hard alloy are preferable at room temperature, temperature increase after, FCC phases due to
Slip system is more, is easy to soften, carbide cutting performance still can drastically decline, such as China Patent Publication No. CN
It discloses in 103173673 A and is proposed through additive come to Co-Ni in the hard alloy system that Co-Ni alloys make binder
Binder Phase is improved, and slows down the consumption of Binder Phase at room temperature, to extend the service life of hard alloy, but due to bonding
Contain a large amount of nickel in phase, so that FCC is switched to, the purer Co of HCP transformation temperatures is lower, and Binder Phase is changed into FCC phases at lower temperatures,
Soften rapidly with the raising of temperature, greatly reduces the cutting ability under hard alloy high temperature.
Invention content
The technical problem to be solved by the present invention is to overcome the deficiencies in the prior art, provide a kind of at high temperature still with preferable
Cutting ability and mechanical property hard alloy.
In order to solve the above technical problems, technical solution proposed by the present invention is：
A kind of hard alloy, including hard phase and Co Binder Phases contain Cr or/and Mo wherein in Co Binder Phases.Preferably,
Ni is free of in the Co Binder Phases.In the Co Binder Phases element that HCP is converted into FCC transformation temperatures can be reduced without containing Ni etc.；
Contain Cr or/and Mo in Co Binder Phases, the transformation temperature can be improved, ensures that Binder Phase remains as HCP structures at high temperature, improve
The cutting ability and mechanical property of hard alloy.
Above-mentioned hard alloy, it is preferred that the mass content of Cr is the quality of 0%~29%, Mo in the Co Binder Phases
Content is 0%~5%, remaining is Co.It is further preferred that the mass content of Cr is 2%~20%, Mo in the Co Binder Phases
Mass content be 1%~5%, remaining is Co.Applicant passes through the study found that a certain amount of Cr and Mo is added in Binder Phase
The opposite FCC phase transition of HCP for inhibiting Co is can aid in, reduction Binder Phase is reacted with rapidoprint, slows down it to reach
The requirement of loss.But Cr and/or Mo is added in Binder Phase can excessively react with Co, form brittle σ phases or η phases, add
The Cr and/or Mo entered is very few, and the requirement for inhibiting Co phase transition is but not achieved.
Above-mentioned hard alloy, it is preferred that it is 5%~25% that the quality of the Binder Phase, which accounts for hard alloy quality,.
Above-mentioned hard alloy, it is preferred that the hard phase is mainly WC or TiC or the mixture of the two.Or
Other one or more metal carbides that can be used as hard alloy hard phase.
Above-mentioned hard alloy, it is preferred that the preparation process of the hard alloy includes being：First according to each element content into
Row dispensing, then ball milling, granulation, sintering are carried out successively, finally timeliness 5-24 hours under the phase point temperature of binder.After sintering
Hard alloy under corresponding Binder Phase phase point temperature timeliness 5-24 hours, can make Binder Phase be completely reformed into HCP knot
Structure, on the one hand since HCP structures have smaller volume, it is ensured that Binder Phase improves hard phase to the more preferable cladding of hard phase
With the bond strength of Binder Phase, while making the Binder Phase of HCP structures that there is higher mechanical property, improves hard alloy comprehensively
Cutting ability and mechanical property.
Above-mentioned hard alloy, it is preferred that the sintering temperature is higher than 1300 DEG C, reaches the heat preservation duration after sintering temperature
Not less than 30min.
Compared with the prior art, the advantages of the present invention are as follows：
(1) hard alloy of the invention uses the Co Binder Phases without Ni, by being added in the Co Binder Phases without Ni
Cr and/or Mo elements, Co Binder Phases HCP switch to the increase of FCC transformation temperatures, and can preventing Co Binder Phases, HCP changes when the temperature rises
At Co phase bleeds caused by volume expansion after FCC phase transformations, to greatly improve the service life of hard alloy.
(2) hard alloy of the invention, can be significantly by adding Cr and/or Mo elements in the Co Binder Phases without Ni
The stability of the HCP phases of the good Co Binder Phases of mechanical property at high temperature is improved, the high-temperature machining of hard alloy is greatly improved
And hardness.
(3) present invention can greatly improve Co bondings by adding Cr and/or Mo elements in the Co Binder Phases without Ni
Mutually with the wetability of hard phase, sintering cemented carbide performance is improved.
(4) present invention in the Co Binder Phases without Ni by adding Cr and/or Mo elements, since Cr, Mo are in Co
Solution strengthening can greatly improve the mechanical property of Co Binder Phases, improve the hardness and cutting ability of hard alloy.
(5) hard alloy of the invention can improve 10- at room temperature compared to the hardness for being not added with hard alloy
50HV, bending strength improve 50-500MPa, and (400 DEG C or more) hardness can improve 20-40HV at high temperature.
Description of the drawings
Fig. 1 is the crystal structure of hard alloy Co Binder Phases at different temperatures in the prior art.
Fig. 2 is the test chart that hard alloy Co Binder Phases are more than 400 DEG C of phase variable volume expansion processes in the prior art.
Fig. 3 is that hard alloy Co Binder Phases undergo phase transition the mechanism schematic diagram for causing Co to bond phase bleed in the prior art.
Specific implementation mode
To facilitate the understanding of the present invention, present invention work more comprehensively, is meticulously described below in conjunction with preferred embodiment,
But the protection scope of the present invention is not limited to the following specific embodiments.
Unless otherwise defined, all technical terms used hereinafter and the normally understood meaning of those skilled in the art
It is identical.Technical term used herein is intended merely to the purpose of description specific embodiment, is not intended to the limitation present invention
Protection domain.
Except there is a special instruction, the various reagents used in the present invention, raw material be can be commercially commodity or
Person can pass through product made from well known method.
The hard alloy of the present invention, including hard phase and Co Binder Phases, wherein contain Cr and/or Mo in Co Binder Phases；And
Hard phase includes mainly WC or TiC or the mixture of the two, and the average grain diameter of hard phase is less than 1.2 μm.The hard of the present invention closes
Gold preparation process include：Dispensing first is carried out according to each element content, then carries out ball milling, granulation, sintering, wherein hard successively
Phase, the sintering temperature of Binder Phase are higher than 1300 DEG C, reach the heat preservation duration after sintering temperature and are not less than 30min；After sintering according to
The transformation temperature of different Binder Phases carries out ageing treatment (aging time 5-24 hours), to obtain whole HCP phases under phase transition temperature
Binder Phase, improve the high-temperature machining performance of hard alloy.
The bonding phase constituent of hard alloy and performance are shown in (note shown in Tables 1 and 2 in each embodiment of the present invention：In table 1
Mo and Cr contents refer to that it accounts for the mass fraction of Binder Phase, WC content refers to that it accounts for the mass fraction of cemented carbide material；By
The wearability test equipment under at present without high temperature, the wearability with service life of hard alloy are bases at room temperature in table 2
ASTM G65 standards measure).
The bonding phase constituent and room-temperature property of the hard alloy of 1 each embodiment and comparative example of table
The hardness of hard alloy at different temperatures in 2 different embodiments of the invention of table
By the experimental data of Tables 1 and 2 it is found that the hard alloy of the hard alloy of the present invention compared with the prior art is (right
Ratio 1-4), bending strength improves 100-400MPa at room temperature, and wearability improves 1-6 times at room temperature, and service life carries at room temperature
It is 2-7 times high；(400 DEG C or more) hardness can improve 10-20HRA at high temperature.It can be seen that base of the present invention in Co Binder Phases
On plinth, by adding suitable Cr and/or Mo elements, the transformation temperature that Co Binder Phases HCP switchs to FCC is improved, Binder Phase is made to exist
HCP phases are maintained as under high temperature, and since the phase slip system is less, hardness is high, ensure that the mechanics of hard alloy at high temperature
Performance can prevent HCP phases from switching to volume expansion caused by FCC phase transformations with high cutting ability simultaneously as the phase transformation is inhibited
And cobalt phase is made to be lost in, there is excellent cutting ability and longer service life to certifiable hard alloy.
Claims (4)
1. a kind of hard alloy, which is characterized in that including hard phase and Co Binder Phases, wherein in Co Binder Phases containing Cr or/and
Mo；Ni is free of in the Co Binder Phases；
The mass content that the mass content of Cr is 15%, Mo in the Co Binder Phases is 5%, remaining is Co；The hard alloy
Preparation process include be：Dispensing first is carried out according to each element content, then carries out ball milling, granulation successively, 2 are sintered at 1400 DEG C
~3h, finally timeliness 15 hours at 800 DEG C.
2. hard alloy as described in claim 1, which is characterized in that the quality of the Co Binder Phases accounts for hard alloy quality
Percentage is 5%~25%.
3. such as claim 1~2 any one of them hard alloy, which is characterized in that the hard phase be mainly WC or TiC or
The mixture of the two.
4. such as claim 1~2 any one of them hard alloy, which is characterized in that reach the heat preservation duration after sintering temperature
Not less than 30min.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610367856.1A CN105861903B (en) | 2016-05-30 | 2016-05-30 | Hard alloy |
| PCT/CN2016/090697 WO2017206292A1 (en) | 2016-05-30 | 2016-07-20 | Hard alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610367856.1A CN105861903B (en) | 2016-05-30 | 2016-05-30 | Hard alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105861903A CN105861903A (en) | 2016-08-17 |
| CN105861903B true CN105861903B (en) | 2018-08-07 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610367856.1A Expired - Fee Related CN105861903B (en) | 2016-05-30 | 2016-05-30 | Hard alloy |
Country Status (2)
| Country | Link |
|---|---|
| CN (1) | CN105861903B (en) |
| WO (1) | WO2017206292A1 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109280838B (en) * | 2018-11-30 | 2020-11-06 | 宇龙精机科技（浙江）有限公司 | Titanium-cobalt alloy and preparation method thereof |
| CN112853188A (en) * | 2020-12-31 | 2021-05-28 | 株洲硬质合金集团有限公司 | Hard alloy and preparation method and application thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103602871A (en) * | 2013-12-09 | 2014-02-26 | 株洲硬质合金集团有限公司 | High-heat-resistance high-strength hard alloy and preparation method thereof |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5839764A (en) * | 1981-09-02 | 1983-03-08 | Hitachi Metals Ltd | Sintered hard alloy |
| SE9703204L (en) * | 1997-09-05 | 1999-03-06 | Sandvik Ab | Tools for drilling / milling circuit board material |
| JP3762777B1 (en) * | 2004-10-19 | 2006-04-05 | 住友電気工業株式会社 | Cemented carbide |
| JP4746310B2 (en) * | 2004-11-30 | 2011-08-10 | 住友電工ハードメタル株式会社 | Mold |
| CN101462206A (en) * | 2008-09-12 | 2009-06-24 | 郭庆虎 | Carbide alloy welding wire or welding rod as well as manufacturing method and application thereof |
| CN101358314B (en) * | 2008-09-22 | 2010-06-09 | 牡丹江工具有限责任公司 | Multiple M genus cemented carbide |
| CN102234729B (en) * | 2010-04-23 | 2013-07-03 | 河南省大地合金股份有限公司 | Preparation method for hard metal |
| CN103602870B (en) * | 2013-10-30 | 2015-08-26 | 株洲钻石切削刀具股份有限公司 | There is Wimet of subsphaeroidal WC grain and preparation method thereof |
-
2016
- 2016-05-30 CN CN201610367856.1A patent/CN105861903B/en not_active Expired - Fee Related
- 2016-07-20 WO PCT/CN2016/090697 patent/WO2017206292A1/en active Application Filing
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103602871A (en) * | 2013-12-09 | 2014-02-26 | 株洲硬质合金集团有限公司 | High-heat-resistance high-strength hard alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105861903A (en) | 2016-08-17 |
| WO2017206292A1 (en) | 2017-12-07 |
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Granted publication date: 20180807 Termination date: 20200530 |