CN102560169A - Method for converting hard alloy with suddenly-changing hardness gradient into hard alloy with gradually-changing hardness gradient - Google Patents
Method for converting hard alloy with suddenly-changing hardness gradient into hard alloy with gradually-changing hardness gradient Download PDFInfo
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- CN102560169A CN102560169A CN2012100455794A CN201210045579A CN102560169A CN 102560169 A CN102560169 A CN 102560169A CN 2012100455794 A CN2012100455794 A CN 2012100455794A CN 201210045579 A CN201210045579 A CN 201210045579A CN 102560169 A CN102560169 A CN 102560169A
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Abstract
The invention discloses a method for converting a hard alloy with a suddenly-changing hardness gradient into a hard alloy with a gradually-changing hardness gradient. In the method, through subsequent liquid-phase multi-burning processing on a WC-Co gradient hard alloy with a cobalt-poor high-hardness surface layer area and a cobalt-rich low-hardness transitional layer area, the aims of eliminating a low-hardness gradually-changing area, realizing gradual change of a medium hardness of the alloy hardness and further improving the wear resistance and the service life of the alloy are achieved; the subsequent liquid-phase multi-burning processing refers to preserving heat of an original gradually-changing WC-Co gradient hard alloy for 60 to 120 min at the temperature of 1400 to 1460 DEG C; and the gradual change of the hardness refers to the slow reduction of the hardness of the alloy from the surface to the inside. The invention discloses the method for converting the WC-Co gradient hard alloy with the suddenly-changing hardness gradient into the WC-Co gradient hard alloy with the gradually-changing hardness gradient so as to prolong the service life of an alloy tool.
Description
Technical field
The present invention relates to a kind of method that the hardness mutant is changed into hardness gradation type gradient hard alloy.
Background technology
Wearing and tearing are a kind of typical manifestation that carbamide tool lost efficacy.The hardness and wear resistance of wimet has positive correlation, improves alloy wear-resisting property and at first must improve hardness of alloy.To the WC-Co wimet, reduce the Co content in the wimet, can significantly improve alloy rigidity, improve alloy wear-resisting property.The graded of Co will inevitably cause the graded of hardness in the alloy in the wimet.
The hardness and the toughness of tradition wimet are a pair of conflicting parameters, and improving hardness will be cost to sacrifice toughness, and vice versa.1986, Sweden Sandvik company took the lead in having released the new material of a kind of wimet-double structure WC-Co gradient hard alloy, was called for short DP (dual phase) alloy.This alloy has successfully solved the hardness of wimet and the contradiction that toughness is difficult to take into account simultaneously, can make alloy work-ing life be improved significantly.This technology mainly comprises two aspects; Promptly at first make the WC+ β+η three-phase contexture alloy (β: Co base bonding phase) that contains even, tiny and the controlled decarburization phase of volume(tric)fraction (η phase); Then this alloy is carried out carburizing treatment, to obtain to have the graded alloy of double structure.The top layer of this alloy and intermediate layer are WC+ β two-phase structure alloy, and the alloy core is WC+ β+η three-phase contexture alloy.Alloy surface is poor Co district; Co content changes in gradient in the alloy transition layer, is rich Co district.The formation mechanism of Co gradient mainly is to be that Co mass transfer takes place motivating force is provided in the alloy through the carbon potential difference in the DP alloy; Promptly through low-carbon alloy is carried out carburizing treatment, make in the WC-Co wimet Co from the low-carbon (LC) district migration of high-carbon regions to alloy of alloy surface.Adopt the alloy surface thickness of this method preparation to be generally 1mm～3mm, it is about 3% to contain Co, gives alloy high firmness and high-wearing feature; The middle transition layer thickness is generally 1.5mm～2.5mm, and the highest Co amount of containing is given the alloy H.T. usually about 10%.Fig. 1 has showed a kind of typical DP alloy polishing section (along the facet at alloy middle part) little load vickers hardness hv 2 (2kgf load) change curve.Adopt the alloy of this technology preparation to exist high firmness district, top layer thickness less than normal, transition layer is the defective of soft saltation zone.After if surperficial high firmness district is worn, the alloy tool life-span can reduce rapidly, thereby has limited applying of alloy.
Summary of the invention
Technical problem to be solved by this invention provides a kind of hardness mutant WC-Co gradient hard alloy and changes hardness gradation type WC-Co gradient hard alloy into, to improve the alloy tool method that the hardness mutant is changed into hardness gradation type gradient hard alloy in work-ing life.
In order to solve the problems of the technologies described above; The method that the hardness mutant is changed into hardness gradation type gradient hard alloy provided by the invention; Through carrying out the following liquid-phase resintering and handle to having poor cobalt high firmness rim surface zona, rich cobalt soft transition layer district WC-Co gradient hard alloy; Reach and eliminate the soft saltation zone; Realize the purpose of hardness gradual change in the alloy, described following liquid-phase resintering is handled and is meant in vacuum sintering furnace the temperature insulation 60min～120min of original hardness mutant WC-Co gradient hard alloy at 1400 ℃～1460 ℃.Said hardness gradual change is meant that alloy rigidity presents slow reduction characteristic by table to the lining.
Adopt the method that the hardness mutant is changed into hardness gradation type gradient hard alloy of technique scheme; Through carrying out the following liquid-phase resintering and handle to having poor cobalt high firmness rim surface zona, rich cobalt soft transition layer district WC-Co gradient hard alloy; Reach and eliminate the soft saltation zone; Realize the gradual change of hardness in the alloy, further improve the purpose in alloy wear-resisting property and work-ing life.The stability of Co gradient-structure is controlled by the migration of liquid motivating force in the wimet.The migration of liquid motivating force is determined by factors such as WC grain degree sizes in liquid phase volume mark, alloy carbon content, the alloy in the alloy jointly.Owing to have carbon potential difference and WC grain degree difference in the original mutant gradient attitude alloy; Receive the influence of factors such as rim surface zona migration of liquid passage is narrow simultaneously; The Co in original rich cobalt transition layer district is only to the alloy core migration in the resintering process, thus make in the alloy Co content by table raise gradually to the lining, alloy rigidity reduces to the lining by table gradually.
In sum, the present invention is that a kind of hardness mutant WC-Co gradient hard alloy changes hardness gradation type WC-Co gradient hard alloy into, to improve the alloy tool method that the hardness mutant is changed into hardness gradation type gradient hard alloy in work-ing life.
Description of drawings
Fig. 1 is little load vickers hardness hv 2 change curves of a kind of typical DP alloy polishing section.
Fig. 2 is 1460 ℃ of preparing methods of the present invention, DP alloy polishing section changes in hardness curve before and after the insulation 120min vacuum resintering.
Fig. 3 is 1430 ℃ of preparing methods of the present invention, and DP alloy polishing section is by the diagonal angle crackle of table different sites HV50 impression to the lining behind the insulation 90min vacuum resintering; (a) and (b): top layer; (c), (d): middle part; (e), (f) core (containing the η phase).
Fig. 4 is 1400 ℃ of preparing methods of the present invention, DP alloy polishing section changes in hardness curve before and after the insulation 60min vacuum resintering.
Embodiment
Below in conjunction with accompanying drawing and embodiment the present invention is described further.
Embodiment 1:
The ZZ22 type DP post tooth that the little load vickers hardness hv 2 of polishing section is Fig. 1 variation carries out the resintering processing in vacuum sintering furnace, the resintering temperature is 1460 ℃, and soaking time is 120min.By with resintering before same sampling, sample preparation measure the vacuum resintering with metering system and handle back alloy polishing section by the little load vickers hardness hv of showing to the lining 2.Observe the vacuum resintering and handle back alloy polishing section, visible 3 different layer regions of tangible reflective characteristic.Fig. 2 has showed vacuum resintering front and back DP alloy polishing section changes in hardness curve.Can know by Fig. 2; The soft saltation zone disappears in the alloy after resintering is handled; Alloy rigidity presents slow reduction characteristic by table to the lining; The hardness of alloy surface is further enhanced, and in the regional extent of the about 5.7mm of first hardness measurement point of alloy surface, resintering is handled the back hardness of alloy and all is higher than former primary state hardness of alloy before the processing.
Embodiment 2:
The ZZ22 type DP post tooth that the little load vickers hardness hv 2 of polishing section is Fig. 1 variation carries out the resintering processing in vacuum sintering furnace, the resintering temperature is 1430 ℃, and soaking time is 90min.By with resintering before same sampling, sample preparation measure the vacuum resintering with metering system and handle back alloy polishing section by the little load vickers hardness hv of showing to the lining 2.Observe the vacuum resintering and handle back alloy polishing section, visible 3 different layer regions of tangible reflective characteristic.DP alloy polishing section changes in hardness curve behind the measurement vacuum resintering; The result shows that after resintering is handled the soft saltation zone disappears in the alloy; Alloy rigidity presents slow reduction characteristic by table to the lining; The hardness of alloy surface is further enhanced, and in the regional extent of the about 5.6mm of first hardness measurement point of alloy surface, resintering is handled the back hardness of alloy and all is higher than former primary state hardness of alloy before the processing.DP alloy polishing section was by the diagonal angle crackle of showing different sites HV50 (50kgf load) impression to the lining after Fig. 3 had showed the vacuum resintering.
Palmqvist fracture toughness property by formula (1) is calculated:
K
IC＝A·H
0.5·(P/∑L)
0.5 (1)
In the formula: H-Vickers' hardness, MPa; The P-applied load, N; ∑ L-diagonal angle crackle total length, mm; The A-constant, 0.0028; K
IC-fracture toughness property, MNm
-3/2Or MPam
1/2
The Palmqvist fracture toughness property of tradition WC-Co wimet is usually at 7MNm
-3/2～25MNm
-3/2Between (applied load is usually between 30kgf～50kgf), the Co massfraction is that the Palmqvist fracture toughness property of traditional WC-Co wimet of 8%～9% is usually at 10MNm
-3/2～17MNm
-3/2Between.
Can find out by Fig. 3; Except that the diagonal angle near the indivedual HV50 impressions in top layer exists the crackle of＜40 μ m; Even applied load is up to 50kgf; DP alloy polishing section does not all produce tangible crackle by the diagonal angle of table different sites HV50 impression to the lining behind the vacuum resintering, has exceeded the useful range of Palmqvist fracture toughness property.This phenomenon explanation, because the formation of gradient-structure, alloy has the excellent properties of high firmness and H.T..
Embodiment 3:
The ZZ22 type DP post tooth that the little load vickers hardness hv 2 of polishing section is Fig. 1 variation carries out the resintering processing in vacuum sintering furnace, the resintering temperature is 1400 ℃, and soaking time is 60min.By with resintering before same sampling, sample preparation measure the vacuum resintering with metering system and handle back alloy polishing section by the little load vickers hardness hv of showing to the lining 2.Discovery handles through resintering that the soft saltation zone disappears in the alloy of back, and alloy rigidity is by showing to present slow reduction characteristic to the lining.Observe the vacuum resintering and handle back alloy polishing section, visible 3 different layer regions of tangible reflective characteristic.Fig. 4 has showed vacuum resintering front and back DP alloy polishing section changes in hardness curve.Can know by Fig. 4; The soft saltation zone disappears in the alloy after resintering is handled; Alloy rigidity presents slow reduction characteristic by table to the lining; The hardness of alloy surface is further enhanced, and in the regional extent of the about 5.4mm of first hardness measurement point of alloy surface, resintering is handled the back hardness of alloy and all is higher than former primary state hardness of alloy before the processing.
Claims (2)
1. method that the hardness mutant is changed into hardness gradation type gradient hard alloy; Carry out the following liquid-phase resintering and handle having poor cobalt high firmness rim surface zona, rich cobalt soft transition layer district WC-Co gradient hard alloy; Eliminate the soft saltation zone; Realize the gradual change of hardness in the alloy, it is characterized in that: described following liquid-phase resintering is handled and is meant in vacuum sintering furnace the temperature insulation 60min～120min of original hardness mutant WC-Co gradient hard alloy at 1400 ℃～1460 ℃.
2. according to claim 1ly change the hardness mutant method of hardness gradation type gradient hard alloy into, it is characterized in that: said hardness gradual change is meant that alloy rigidity presents slow reduction characteristic by table to the lining.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9157136B2 (en) | 2012-12-05 | 2015-10-13 | Industrial Technology Research Institute | Multi-element alloy material and method of manufacturing the same |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN85108173A (en) * | 1984-11-13 | 1986-05-10 | 桑特拉德有限公司 | Be suitable for most the cemented carbide body of rock-boring and ore cutting |
| US5453241A (en) * | 1991-02-05 | 1995-09-26 | Sandvik Ab | Cemented carbide body with extra tough behavior |
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2012
- 2012-02-27 CN CN2012100455794A patent/CN102560169A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN85108173A (en) * | 1984-11-13 | 1986-05-10 | 桑特拉德有限公司 | Be suitable for most the cemented carbide body of rock-boring and ore cutting |
| US5453241A (en) * | 1991-02-05 | 1995-09-26 | Sandvik Ab | Cemented carbide body with extra tough behavior |
Non-Patent Citations (2)
| Title |
|---|
| 《Scripta Materialia》 20051231 Zhigang Zak Fang et al. Liquid phase sintering of functionally graded WC-Co composites 第52卷, * |
| ZHIGANG ZAK FANG ET AL.: "Liquid phase sintering of functionally graded WC–Co composites", 《SCRIPTA MATERIALIA》 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9157136B2 (en) | 2012-12-05 | 2015-10-13 | Industrial Technology Research Institute | Multi-element alloy material and method of manufacturing the same |
| TWI555856B (en) * | 2012-12-05 | 2016-11-01 | 財團法人工業技術研究院 | Multi-element alloy material and method of manufacturing the same |
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Application publication date: 20120711 |