CN104513924A - Preparation method for high-strength cemented carbide employing iron and nickel as substitutes of cobalt - Google Patents
Preparation method for high-strength cemented carbide employing iron and nickel as substitutes of cobalt Download PDFInfo
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- CN104513924A CN104513924A CN201310453591.3A CN201310453591A CN104513924A CN 104513924 A CN104513924 A CN 104513924A CN 201310453591 A CN201310453591 A CN 201310453591A CN 104513924 A CN104513924 A CN 104513924A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
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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
- C22C29/08—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 based on tungsten carbide
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Abstract
A preparation method for high-strength cemented carbide employing iron and nickel as substitutes of cobalt comprises the following steps: step 101, performing ball milling according to the WC:FeNiCo weight ratio of 2:1 to 3:1; step 102, performing drying and granulation on the press material after ball milling is finished; and step 103, compacting the alloy and performing vacuum sintering. The iron-nickel alloy prepared by employing the preparation method for the high-strength cemented carbide employing iron and nickel as substitutes of cobalt possesses a high-strength good-impact-resistance structure under a common vacuum sintering condition, and is an ideal material for replacing YG20C. During sintering, the cementation metal has good WC wettability and is relatively strong in liquid filling capability, equipment employed in the manufacture technology is substantially same to equipment for manufacturing conventional cemented carbide, and the cost of updating the production line is well saved.
Description
Technical field
The invention belongs to metallurgical manufacture field, relate to a kind of high-strength iron nickel for cobalt hard alloy preparation method.
Background technology
Research at present to cold pier cold-punching mould, its main damage form has two kinds, one is wear-out failure, mainly sweep away in continuous upsetting repeatedly, the friction of workpiece and mould and cause the wearing and tearing of grinding tool, the destruction that dimension overproof causes, another kind is cracking destruction, major cause is under repeated stock, makes mould fatigue cracking..When numerous, cracking is the main damage form of mould.The fatigue performance of strengthening mould and shock resistance become the main path in work-ing life.For Wimet, strengthen the length of free path exactly on the left branch line of alloy, to improve intensity, alloy rigidity declines to some extent simultaneously.The hardness of alloy is the guarantee that mould has excellent abrasive resistance.High hardness and mould fragility is strengthened, shock resistance just reduces, and result in mould easy to crack, low hardness can not meet service requirements.High hardness value should be kept to meet the bending strength of alloy mold again enough high, selection is very important.In the selection of alloy, high cobalt alloy YG20 or YG20C just becomes the preferred material of cold pier cold-punching mold, widespread use in the industry, and facts have proved that the destruction of YG20 and YG20C material is seldom the problem of dimension wears, and be often the destruction-cracking destruction of the second form, so want to improve the mold use life-span, be just summed up as the bending strength and shock resistance that improve material.
The bending strength of high-cobalt hart metal and shock resistance will be good than low cobalt alloy many, but also increase the cost of alloy.Although select high-cobalt hart metal YG20 and YG20C to be the first-selection of cold pier cold-punching mold material, its over-all properties is also good than other alloy, and practice also demonstrates this point.Its common collapse mode of widely used YG20 and YG20C cold pier cold-punching mold remains cracking destruction, and meanwhile, expensive due to cobalt, its application is also restricted.
Summary of the invention
For overcoming traditional high-cobalt hart metal bending strength and shock resistance deficiency, the technological deficiency of cost intensive, the invention provides a kind of high-strength iron nickel for cobalt hard alloy preparation method simultaneously.
High-strength iron nickel, for cobalt hard alloy preparation method, comprises the steps:
Step 101 is prepared burden ball milling: carry out ball milling according to the proportioning of part by weight WC:FeNiCo=2:1 to 3:1, WC is wolfram varbide;
Step 102, to binder drying and granulating after ball milling completes;
Step 103 suppresses alloy and vacuum sintering.
Preferably, wet-milling mode is adopted during ball milling in described step 101.
Concrete, in described step 101, the wet-milling time is no less than 20 hours.
Preferably, part by weight WC:FeNiCo=7:3 in described step 101.
Preferably, pressure when described step 103 is suppressed is 150-350 MPa.
Preferably, in described step 103, sintering temperature is 1360-1400 degree Celsius.
Adopt the iron-nickel alloy that high-strength iron nickel of the present invention obtains for cobalt hard alloy preparation method, under the condition of conventional vacuum sintering, can obtain the weave construction that intensity is high, shock resistance is good, be the ideal material of alternative YG20C.In sintering process, Binder metal is good to WC wettability, and liquid phase filling capacity is comparatively strong, and the equipment used in process for making is roughly the same with conventional rigid alloy, well can save the cost upgrading production line.
Embodiment
Below the specific embodiment of the present invention is described in further detail.
At present, Fe, Ni also often appear in Hardmetal materials as cementing phase, but still can not replace cobalt completely.Fe, Co, Ni are same gang element, the phasor formed with WC is also quite similar, and to the wettability of WC, cobalt, nickel are the same in a vacuum, wetting angle equals zero, and iron is poor, solubleness is also different, and the molten WC of Ni is 12 ~ 20%, Co is 10 ~ 15%, and Fe is minimum, recrystallization speed when it must have influence on sintering, cementing consolidation strength with WC and grain size, thus affect alloy strength performance.Thus improve wettability and also will become the effective means improving alloy strength.
In Fe, add the Ni of some amount, can improve the wettability of cementing relative WC, meanwhile, Fe and Ni forms unlimited solid solution, and Fe can be made to be strengthened.Practice shows, the cementing alloy property made mutually of iron nickel of Fe:Ni=3:1 is best.Easily there is η phase in this its tissue of cementing Wimet, in order to prevent the appearance of η phase, a small amount of carbon black can be added in compound, simultaneously also can reinforced iron-base tissue.In order to the cementing phase of alloying and raising add a certain amount of Co powder with the strength of joint of WC, show in the microhardness result of Co-WC and Ni-WC sosoloid, it is larger that cobalt compares nickel phase strengthening effect, and Co and Fe, Ni all can form unlimited solid solution, make cementing wetting improvement further and strengthening mutually, by the optimization of this weave construction of alloy, alloy is greatly enhanced work-ing life.
According to above-mentioned analysis, for the collapse mode that cold pier cold-punching mould is common, be that main binding mutual-assistance alloy microstructure improves with Fe-Ni-Co, reinforced alloys performance, development high-strength iron nickel is for the strength materials of cobalt.
Embodiment
(1) prepare burden ball milling: WC70%-FeNiCo30%, granularity-200 order.Ratio of grinding media to material 3:1, wet-milling 20h, vacuum-drying, mixes glue and granulates.WC is wolfram varbide.
(2) compacting and sintering: compacting A standard specimen (5 × 5 × 30mm) and nail clip mould.
Wherein determine the pressing pressure (150-350Mpa) that is suitable for and shrinkage coefficient (1.18-1.25), vacuum sintering temperature (1360-1400 DEG C).
(1) densification process of this alloy sintering
The necessary factor affecting densification process is exactly the wetting angle between liquid-solid phase, and the capillary pressure of liquid improves along with the reduction of the wetting angle to WC particle, and the ability that thus liquid phase fills aperture is improved along with the reduction of the wetting angle to solid phase.Secondly be the quantity of liquid phase, when amount of liquid phase is no more than 50%, capillary pressure improves along with the increase of amount of liquid phase.Meanwhile, the resistance to flow of WC particle then increases with it and reduces.With regard to this material, its cementing phase composition is about 30%, and Ni, Co molten WC ability is larger, therefore, the enhanced dissolution rate of WC, adds the liquid phase of sintering, usual amount of liquid phase remains on 15 ~ 36% and is advisable, and thus, is enough to ensure that densification process has enough liquid phases.Ensure that the coated current downflow of WC particle in liquid phase, complete dissolving, precipitation, solid state sintering three process, make its complete densification, finally reach the object of sintering.In an experiment, have the alloy of microscopic defect to make up completely, macrostructure observe and carrying out flaw detection without any defect, illustrate that this material wets improves, stowing capacity strengthened.
(2) impact of sintering temperature alloy performance
The amount of liquid phase of sintered compact increases with the raising of sintering temperature, with regard to this material, because Fe-Co-Ni forms unlimited solid solution, effective crystallization range is narrower, and when sintering temperature slightly changes, the concentration tonsure of liquid phase will change greatly, experimental result shows, within the scope of 1360-1380 DEG C, performance is more stable, when reaching 1400 DEG C, more than bending strength decline 500Mpa, and sample edges of the periphery rust, illustrate that wandering tendency exists, temperature is higher again, may produce lower seat.Illustrate that this material sintering temperature interval is narrower thus, comparatively large to temperature sensitivity, should strictly control aborning.
(3) each element effect in the alloy
Carbon mainly suppresses the appearance of the crisp hard phase very easily produced in the cementing alloy of Fe-Ni, and strengthens cementing phase, and the height of its quantity also affects the height of sintering temperature.Co, Ni improve the wettability of Fe to WC, Co be solid-solution in cementing mutually in serve " pinning " effect, stop dislocation motion, strengthening matrix, optimizing tissue structure, makes cementingly to strengthen mutually, ensures that densification process is complete.
(4) strength characteristics
Bending strength weighs an important indicator of Wimet, and it is a mark of alloy ductility.Bending strength is high, and its good toughness is described, shock resistance is good.This material sintered state intensity A scale monodrome reaches 3370Mpa, average out to 2880Mpa.
More than comprehensive, adopt the iron-nickel alloy that high-strength iron nickel of the present invention obtains for cobalt hard alloy preparation method, under the condition of conventional vacuum sintering, can obtain the weave construction that intensity is high, shock resistance is good, be the ideal material of alternative YG20C.In sintering process, Binder metal is good to WC wettability, and liquid phase filling capacity is comparatively strong, and the equipment used in process for making is roughly the same with conventional rigid alloy, well can save the cost upgrading production line.
Above-describedly be only the preferred embodiments of the present invention, described embodiment is also not used to limit scope of patent protection of the present invention, and the therefore equivalent structure change done of every utilization description of the present invention, in like manner all should be included in protection scope of the present invention.
Claims (6)
1. high-strength iron nickel is for cobalt hard alloy preparation method, comprises the steps:
Step 101 is prepared burden ball milling: carry out ball milling according to the proportioning of part by weight WC:FeNiCo=2:1 to 3:1, WC is wolfram varbide;
Step 102, to binder drying and granulating after ball milling completes;
Step 103 suppresses alloy and vacuum sintering.
2. high-strength iron nickel, for a cobalt hard alloy preparation method, is characterized in that as claimed in claim 1, adopts wet-milling mode in described step 101 during ball milling.
3. high-strength iron nickel, for a cobalt hard alloy preparation method, is characterized in that as claimed in claim 2, and in described step 101, the wet-milling time is no less than 20 hours.
4. high-strength iron nickel, for a cobalt hard alloy preparation method, is characterized in that as claimed in claim 1, part by weight WC:FeNiCo=7:3 in described step 101.
5. high-strength iron nickel, for a cobalt hard alloy preparation method, is characterized in that as claimed in claim 1, and pressure when described step 103 is suppressed is 150-350 MPa.
6. high-strength iron nickel, for a cobalt hard alloy preparation method, is characterized in that as claimed in claim 1, and in described step 103, sintering temperature is 1360-1400 degree Celsius.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310453591.3A CN104513924A (en) | 2013-09-29 | 2013-09-29 | Preparation method for high-strength cemented carbide employing iron and nickel as substitutes of cobalt |
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| CN201310453591.3A CN104513924A (en) | 2013-09-29 | 2013-09-29 | Preparation method for high-strength cemented carbide employing iron and nickel as substitutes of cobalt |
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| CN104513924A true CN104513924A (en) | 2015-04-15 |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108085556A (en) * | 2017-12-21 | 2018-05-29 | 洛阳名力科技开发有限公司 | A kind of preparation method of WC-Fe-Ni-Co hard alloy |
| CN113493879A (en) * | 2021-06-21 | 2021-10-12 | 莱芜职业技术学院 | Iron-nickel cobalt-substituted hard alloy ultrathin circular blade |
-
2013
- 2013-09-29 CN CN201310453591.3A patent/CN104513924A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108085556A (en) * | 2017-12-21 | 2018-05-29 | 洛阳名力科技开发有限公司 | A kind of preparation method of WC-Fe-Ni-Co hard alloy |
| CN113493879A (en) * | 2021-06-21 | 2021-10-12 | 莱芜职业技术学院 | Iron-nickel cobalt-substituted hard alloy ultrathin circular blade |
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Application publication date: 20150415 |