CN106756599A - The preparation method of cBN High Speed Steel Composites and cBN High Speed Steel Composites - Google Patents
The preparation method of cBN High Speed Steel Composites and cBN High Speed Steel Composites Download PDFInfo
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- CN106756599A CN106756599A CN201611231736.5A CN201611231736A CN106756599A CN 106756599 A CN106756599 A CN 106756599A CN 201611231736 A CN201611231736 A CN 201611231736A CN 106756599 A CN106756599 A CN 106756599A
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- 229910000997 High-speed steel Inorganic materials 0.000 title claims abstract description 137
- 239000002131 composite material Substances 0.000 title claims abstract description 91
- 238000002360 preparation method Methods 0.000 title claims description 30
- 239000000843 powder Substances 0.000 claims abstract description 187
- 239000000203 mixture Substances 0.000 claims abstract description 73
- 239000002243 precursor Substances 0.000 claims abstract description 60
- 239000002184 metal Substances 0.000 claims abstract description 32
- 229910052751 metal Inorganic materials 0.000 claims abstract description 32
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 23
- 230000000737 periodic effect Effects 0.000 claims abstract description 22
- 229910052742 iron Inorganic materials 0.000 claims abstract description 19
- 239000002245 particle Substances 0.000 claims description 32
- 238000005245 sintering Methods 0.000 claims description 30
- 238000000498 ball milling Methods 0.000 claims description 21
- 239000000463 material Substances 0.000 claims description 20
- 238000000034 method Methods 0.000 claims description 18
- 238000000137 annealing Methods 0.000 claims description 14
- 238000009413 insulation Methods 0.000 claims description 12
- 238000000227 grinding Methods 0.000 claims description 10
- 239000002994 raw material Substances 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 8
- 238000012856 packing Methods 0.000 claims description 8
- 238000000280 densification Methods 0.000 claims description 7
- 229910003178 Mo2C Inorganic materials 0.000 claims description 6
- 229910003470 tongbaite Inorganic materials 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 4
- 238000010791 quenching Methods 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052721 tungsten Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 238000010792 warming Methods 0.000 claims description 2
- 238000003763 carbonization Methods 0.000 claims 2
- 230000005496 eutectics Effects 0.000 abstract description 5
- 239000007788 liquid Substances 0.000 abstract description 4
- 230000003628 erosive effect Effects 0.000 abstract description 3
- 239000007791 liquid phase Substances 0.000 abstract description 2
- 230000006641 stabilisation Effects 0.000 abstract description 2
- 238000011105 stabilization Methods 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 15
- 230000008569 process Effects 0.000 description 14
- 238000002156 mixing Methods 0.000 description 8
- 230000006872 improvement Effects 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 6
- 239000011230 binding agent Substances 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 229910052582 BN Inorganic materials 0.000 description 3
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000007790 solid phase Substances 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910009043 WC-Co Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 239000003292 glue Substances 0.000 description 2
- 238000013001 point bending Methods 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000009833 condensation Methods 0.000 description 1
- 230000005494 condensation Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000012188 paraffin wax Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000011214 refractory ceramic Substances 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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)
Abstract
Prepare the high-speed steel precursor mixture of powders of cBN High Speed Steel Composites, the high-speed steel precursor mixture of powders including Co powder that mass fraction is 3~15%, 32~75% Fe powder, 20~50% metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race carbide powder, 0~2% C powder.CBN High Speed Steel Composites include cBN, 2.7~13.5% Co, 1.7~5.4% C, 14~45% metal, 40.6~67.5% Fe selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race that mass fraction is 1~30%.Atomized powder is replaced by the powder using non-atomized, the local eutectic liquid phase that can be avoided the occurrence of prevents local eutectic liquid from producing erosion with respect to cBN, cBN is kept stabilization, so as to lift the performance of final cBN High Speed Steel Composites.
Description
Technical field
Before the technical field of cBN, more particularly to a kind of high-speed steel for preparing cBN- High Speed Steel Composites
Body mixture of powders, the cBN- High Speed Steel Composites prepared by the high-speed steel precursor mixture of powders and should
The preparation method of cBN- High Speed Steel Composites.
Background technology
With car generation wear into as development trend, and superhard material processing and finishing requirement more and more higher when, it is superhard
The development of material cutter is extremely crucial.Cubic boron nitride (cBN) cutter has extremely outstanding performance, traditional glomerocryst cBN
The preparation of sintered body is mainly prepared using superhigh temperature-superelevation platen press, a kind of high-ductility that such as CN104525935A is announced
Property cubic boron nitride sintered material and preparation method thereof, the pressure typically up to 4000~8000MPa needed for preparation process, and
Then up to 1300~1900 DEG C of sintering temperature.Realize that the high pressure of powder is fine and close due to needing the graphite jig of certain regular size
, there is sintering in the conventional way efficiency be low, high cost, sintered dimensions and shape are restricted (mostly disc-shaped, cylinder in change process
Shape) the shortcomings of, so as to cause the price of cBN sintered body products higher.Moreover, due to cBN extreme hardness (7200~
9800HV), the grinding difficulty of its sintered blank is larger, therefore wants hot pressing is specific for the sintered blank of regular shape is processed into
The manufacturing cost of the workpiece of complicated shape is higher.
The Binder Phase of conventional cBN composites includes TiN, TiC, AlN, Co, WC-Co etc., and the high temperature of these Binder Phases burns
Junction characteristic so that the preparation process of cBN composites must be aided with high pressure and just be avoided that generation cBN → hBN (hexagonal boron nitride)
Transformation.And some compared with low melting point bonding mutually such as Al, although the preparation of low temperature cBN composites can be realized, but used
When temperature is raised, Binder Phase softens, and causes cBN abrasion of particles to be sharply increased with quantity is peeled off.With reference to cBN to iron based compacts
Chemical inertness advantage, from high alloy high-speed steel as new cBN Binder Phases, can both ensure its processing temperature higher than general
Low-melting-point metal, be unlikely to occur the phenomenon that matrix softens too early, it is also ensured that its relatively low burning compared with refractory ceramic
Junction temperature.
But, the sintering temperature of traditional high alloy high-speed steel atomized powder also above 1250 DEG C, its traditional super solid phase liquid
The local eutectic liquid that phase sintering process (SLPS) occurs to be met and produce erosion to cBN, i.e., reacted with cBN and cause cBN to decompose.Cause
This, need to improve the preparation technology of cBN to optimize its production efficiency and production cost, or develop a kind of novel processing step.This
Application proposes to prepare cBN- High Speed Steel Composites without pressure solid-phase sintering process from new non-atomized powder.
The content of the invention
Based on above-mentioned the deficiencies in the prior art, the technical problems to be solved by the invention be to provide a kind of production efficiency it is high,
Low production cost without pressure solid phase sintering process, and using the method prepare densification degree it is high, product size is diversified,
The cBN- High Speed Steel Composites of excellent performance.Also provide the high-speed steel precursor powder for implementing to be used during the preparation method
Mixture and preparation method thereof, cBN- High Speed Steel Composites precursor mixture of powders and preparation method thereof.
The technical scheme that present invention solution above-mentioned technical problem is used is as follows：
The high-speed steel precursor mixture of powders of cBN- High Speed Steel Composites is prepared, the high-speed steel precursor powder is mixed
Compound including Co powder that mass fraction is 3~15%, 32~75% Fe powder, 20~50% selected from the race of the periodic table of elements the 4th,
The carbide powder of the metal of the 5th race and the 6th race, 0~2% C powder.Atomized powder is replaced by the powder using non-atomized, can
The local eutectic liquid phase for avoiding the occurrence of, prevents local eutectic liquid from producing erosion with respect to cBN, cBN is kept stabilization, so as to be lifted most
The performance of whole cBN- High Speed Steel Composites.
As the further improvement of the above-mentioned high-speed steel precursor mixture of powders for preparing cBN- High Speed Steel Composites：Institute
The carbide powder stated selected from the metal of the race of the periodic table of elements the 4th, the 5th race and the 6th race includes WC powder, Mo2C powder, Cr3C2Powder and VC
Powder, mass ratio W in the carbide powder：Mo：Cr：V is (8~12)：(3.5~6.5)：(2.5~5.5)：(0~20).These
The carbon dissociated in metal carbides carries out oxidation reaction and has purified metal carbides and Fe with Fe powder, the oxygen at Go powder particles interface
The granular boundary of powder, Go powder, improves both interface bond strengths.When using the carbide constituted with aforementioned proportion, institute
The cBN- High Speed Steel Composites for obtaining have most excellent performance.
As the further improvement of the above-mentioned high-speed steel precursor mixture of powders for preparing cBN- High Speed Steel Composites：Institute
Stating high-speed steel precursor mixture of powders includes Co powder, 50~64% Fe powder, 25~39% that mass fraction is 7~11%
Selected from carbide powder, 0~2% C powder of the metal of the race of the periodic table of elements the 4th, the 5th race and the 6th race；Matter in the carbide powder
Amount compares W：Mo：Cr：V is (9.5~10.5)：(4.5~5.5)：(3.5~4.5)：(7~13).
The preparation method of high-speed steel precursor powder mixture：Include matter according to the high-speed steel precursor mixture of powders
Amount fraction be 3~15% Co powder, 32~75% Fe powder, 20~50% selected from the race of the periodic table of elements the 4th, the 5th race and the 6th
The carbide powder of the metal of race, the proportioning of 0~2% C powder weigh raw material, then by various raw materials in ball mill with (4~
6)：1 ratio of grinding media to material, 0.4~0.8 packing factor, the ball milling speed of 20~30 turns/min, carry out the ball milling of 24~48h, that is, make
It is standby to obtain high-speed steel precursor powder mixture；Ball milling is carried out in the range of above-mentioned parameter, can be made various in mixture of powders
Feed distribution is uniform, is difficult segregation, is easy to be compressed to variously-shaped pressed compact, the traditional powder by atomization technique of can effectively replace.
Mix with cBN powder again after high-speed steel precursor mixture of powders is first well mixed, can simultaneously realize the uniform mixing of the two
With primary adhesion, the powder segregation in transport process is prevented.
CBN- High Speed Steel Composites precursor powder mixtures, including mass fraction is the above-mentioned high-speed steel of 70-99%
Precursor powder mixture powder and 1~30% cBN powder.Its preparation method includes step：1) high-speed steel precursor powder is prepared
Mixture；2) according to containing the high speed that mass fraction is 70~99% in cBN- High Speed Steel Composites precursor powder mixtures
Steel precursor powder mixture powder, the proportioning of 1~30% cBN powder weigh the high-speed steel precursor powder mixture and cBN
Powder, then by two kinds of raw materials in ball mill with (0.5~1.5)：1 ratio of grinding media to material, 0.4~0.8 packing factor, 20~30
Turn/the ball milling speed of min, carry out the ball milling of 6~10h, that is, prepare the mixing of cBN- High Speed Steel Composites precursor powder
Thing.
CBN- High Speed Steel Composites, i.e., it is a kind of with high-speed steel as Binder Phase, composites of the cBN as hard phase, including
Mass fraction be 1~30% cBN, 2.7~13.5% Co, 1.7~5.4% C, 14~45% selected from the periodic table of elements
Metal, 40.6~67.5% Fe of the 4th race, the 5th race and the 6th race.
It is described selected from the race of the periodic table of elements the 4th, the 5th race as the further improvement of above-mentioned cBN- High Speed Steel Composites
Metal with the 6th race includes W, Mo, Cr and V, mass ratio W in the metal：Mo：Cr：V is (8~12)：(3.5~6.5)：
(2.5~5.5)：(0~20).
Used as the further improvement of above-mentioned cBN- High Speed Steel Composites, the cBN- High Speed Steel Composites include quality
Fraction be 5~20% cBN, 6.3~9.9% Co, 1.7~5.4% C, 20.7~31.5% selected from the periodic table of elements
Metal, 45~57.6% Fe of the 4th race, the 5th race and the 6th race；Mass ratio W in the metal：Mo：Cr：V for (9.5~
10.5)：(4.5~5.5)：(3.5~4.5)：(7~13).
As the further improvement of above-mentioned cBN- High Speed Steel Composites, cBN in the cBN- High Speed Steel Composites
Average grain diameter be 0.5-50 μm, using the cBN of the particle diameter can make cBN- High Speed Steel Composites possess consistency higher and
Hardness；The cBN- High Speed Steel Composites include the different cBN of at least two particle diameters, now, two kinds of cBN phase interworkings of particle diameter
Close, less particle can fill the gap that larger particle is formed, the premise of higher-density and hardness can kept
Under be substantially reduced cost.
As the further improvement of above-mentioned cBN- High Speed Steel Composites, the grain of the different cBN of at least two particle diameter
Footpath is respectively selected from 0.5 μm, 5 μm, 12 μm, 20 μm, 50 μm.The cBN of above-mentioned particle diameter is easily obtained, and the effect being used in conjunction with each other is most
It is good.
The preparation method of cBN- High Speed Steel Composites, the method including the step of be：
1) high-speed steel precursor powder mixture is prepared：Include quality point according to the high-speed steel precursor mixture of powders
Number for 3~15% Co powder, 32~75% Fe powder, 20~50% selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race
The carbide powder of metal, the proportioning of 0~2% C powder weigh raw material, then by various raw materials in ball mill with (4~6)：1
Ratio of grinding media to material, 0.4~0.8 packing factor, the ball milling speed of 20~30 turns/min, carry out the ball milling of 24~48h, that is, prepare
High-speed steel precursor powder mixture；
2) cBN- High Speed Steel Composites precursor powder mixtures are prepared：According to cBN- High Speed Steel Composites presomas
Matching somebody with somebody containing the high-speed steel precursor powder mixture, 1~30% cBN powder that mass fraction is 70~99% in mixture of powders
Than weighing the high-speed steel precursor powder mixture and cBN powder, then by two kinds of raw materials in ball mill with (0.5~1.5)：
1 ratio of grinding media to material, 0.4~0.8 packing factor, the ball milling speed of 20~30 turns/min, carry out the ball milling of 6~10h, that is, be prepared into
To cBN- High Speed Steel Composites precursor powder mixtures；
3) it is molded：CBN- High Speed Steel Composites precursor powder mixtures are made by pressed compact by hydraulic press；Due to adopting
With the powder of non-atomized, therefore cBN- High Speed Steel Composites precursor powder mixtures can be made various shapes as needed
The pressed compact of shape, such as band relief angle indexable insert tip, throw away tip, stepped hole, annular shape, can be suppressed with near-net-shape and sintering prepares nearly end form
CBN- High Speed Steel Composites instruments；Shaping needed for pressure and the time determined according to the shapes and sizes of pressed compact, generally,
Pressing pressure is 100~200MPa, and the dwell time is 1~10min；
4) vacuum-sintering densification is carried out to pressed compact：Sintering temperature is warming up to the heating rate of 80~120 DEG C/h
1130~1170 DEG C and 0.5~1.5h is incubated, then using going out after rate of temperature fall gradient cooling to the room temperature of 180~220 DEG C/h
Stove；
5) vacuum softening annealing：First at a temperature of 900~950 DEG C be incubated 0.25~0.75h, then with 8~12 DEG C/
The rate of temperature fall of h is cooled to 700~800 DEG C and is incubated 1~2h, then 550 are cooled to the rate of temperature fall of 18~22 DEG C/h~
650 DEG C and 1~2h is incubated, then furnace cooling is to coming out of the stove after room temperature；Further machine can be carried out to pressed compact in annealing softening state
Processing and grinding, can be further processed into the pressed compact with special shape by the pressed compact after the densification of conventional shape.
6) quench：First stage is to be put into the sintering furnace that temperature is 520~560 DEG C, is come out of the stove after insulation tmin, second stage
To be put into the sintering furnace that temperature is 830~870 DEG C, come out of the stove after insulation tmin, the phase III is 1130~1170 to be put into temperature
DEG C sintering furnace, insulation 8~12min after come out of the stove, fourth stage is to be put into the sintering furnace that temperature is 520~560 DEG C, insulation 0.5
Come out of the stove after~1.5h, the 5th stage was to be put into the sintering furnace that temperature is 260~300 DEG C, come out of the stove after 0.5~1.5h of insulation, then
Air cooling is to room temperature；Wherein, t=(1~2) * m, m are the effective dimensions of pressed compact, and unit is mm；For example, when pressed compact is for cylinder,
Corresponding effective dimensions is diameter, and diameter value is 1-50mm；When pressed compact is cuboid, corresponding effective dimensions is thickness, thick
Angle value is 1-40mm.
7) it is tempered：The sintering furnace that temperature is 560~600 DEG C is put into, is come out of the stove after insulation >=1h, be then air cooled to room temperature；
Repeat 2~5 times and obtain cBN- High Speed Steel Composites afterwards, the cBN- High Speed Steel Composites contain mass fraction for 1~
30% cBN, 2.7~13.5% Co, 1.7~5.4% C, 14~45% selected from the race of the periodic table of elements the 4th, the 5th race and
The metal of the 6th race, 40.6~67.5% Fe.
Before the forming, cBN- High Speed Steel Composites precursor powder mixtures can be carried out mixing glue treatment, mixing glue can
Make powder realize being uniformly distributed, mix adhesive process and be specially：Use the mass fraction of paraffin for 3~8% gasoline solution, every
The gasoline solution of 5mL is added in 100gcBN- High Speed Steel Composites precursor powder mixtures, is then stirred dry
Dry, speed of agitator is 30 rev/min, and drying temperature is 60 DEG C, and drying time is 10 minutes, then using the screen cloth mistake of 30 mesh
Sieve.
Step 4) in gradient cooling process be preferably divided into three phases：First stage is to be cooled to 1100 DEG C and be incubated
1h, to be cooled to 1000 DEG C and being incubated 1h, the phase III, to be cooled to 900 DEG C and being incubated 1h, is then cooled to room to second stage
Temperature；Deformation and the micro-crack tendency of pressed compact can be improved by the way of this gradient cooling.
It is described selected from the periodic table of elements as the further improvement of the preparation method of above-mentioned cBN- High Speed Steel Composites
The carbide powder of the metal of 4 races, the 5th race and the 6th race includes WC powder, Mo2C powder, Cr3C2Powder and VC powder, matter in the carbide powder
Amount compares W：Mo：Cr：V is (8~12)：(3.5~6.5)：(2.5~5.5)：(0~20).
The present invention has advantages below：1) ball milling mixing, the high-speed steel of preparation are carried out using element powder and carbide powder
The characteristics of powder has suppression performance excellent and is difficult segregation；2) cBN powder and above-mentioned high-speed steel precursor powder mixture are used
The mode of ball milling mixing mixes cBN powder, can simultaneously realize uniform mixing and the primary adhesion of the two, in preventing transport process
Powder segregation；3) size of the cBN particles for using is related to 0.5 μm, 5 μm, 12 μm, 20 μm, 50 μm, be divided into single particle size add and
Mixing particle diameter adds two ways, can further regulate and control product quality and production cost；4) preparation method can realize material
Without standby, sintered density >=98.5% of the cBN- High Speed Steel Composites of preparation is suppressed, with inexpensive, efficient spy
Point, remote unconventional superhigh temperature super-pressure preparation technology is comparable；5) using the compacting of powder metallurgy near-net-shape and sintering flow, can
Realize prepared by the nearly end form of cBN- High Speed Steel Composites, break away from big and high cost the disadvantage of conventional machining surplus；6) temperature is sintered
Degree is less than 1200 DEG C, and the good stability of cBN, High-Speed Steel Carbide are strong in the adhesion of even dispersion distribution and cBN and high-speed steel；
7) cBN- High Speed Steel Composites also have heat treatable characteristic, can be machined out and grinding in annealing softening state.
Brief description of the drawings
Fig. 1 is the SEM photograph of the cBN- High Speed Steel Composites of embodiment 2.
Fig. 2 is the SEM photograph of the cBN- High Speed Steel Composites of embodiment 3.
Fig. 3 is the SEM photograph of the cBN- High Speed Steel Composites of embodiment 4.
Specific embodiment
Beneficial effects of the present invention are described further by the following examples.
Embodiment 1-5's differs only in：The proportioning of high-speed steel precursor powder mixture is differed, and accordingly cBN- is high
The composition of fast steel composite material is also differed；Embodiment 3,6-9 is differed only in：Carbon in high-speed steel precursor powder mixture
The proportioning of compound is differed, and accordingly the composition of cBN- High Speed Steel Composites is also differed；The difference of embodiment 3,10-13 is only
It is：The proportioning of cBN- High Speed Steel Composites precursor powder mixtures is differed, accordingly cBN- High Speed Steel Composites
Composition also differ；3 are specifically shown in Table, wherein, carbide powder is by WC powder, Mo2C powder, Cr3C2Powder and VC powder are constituted, WC powder,
Mo2C powder, Cr3C2The quality of powder and VC powder is calculated according to the mass ratio of W, Mo, Cr, V.The cBN- high-speed steel of embodiment 1-13 is answered
The composition of condensation material is shown in Table 2.The unit of each component is mass fraction %.
Table 1 is the proportioning of the high-speed steel precursor powder mixture of embodiment 1-13.
Table 2 is the composition of the cBN- High Speed Steel Composites of embodiment 1-13.
Embodiment 3,14-15 is differed only in：The preparation technology of high-speed steel precursor powder mixture is differed；Implement
Example 3,14-15 is differed only in：The preparation parameter of cBN- High Speed Steel Composites precursor powder mixtures is differed；Specifically
3 are shown in Table, wherein, to turn/min, the unit of Ball-milling Time is h to the unit of ball milling speed, and abrading-ball is WC-Co hard alloy.
Table 3 is high-speed steel precursor powder mixture, the cBN- High Speed Steel Composites precursors of embodiment 3,14-17
The preparation parameter of last mixture.
Embodiment 3,18-19 is differed only in：Sintering temperature during sintering densification is different with soaking time, and
Programming rate is 100 DEG C/h, and rate of temperature fall is 200 DEG C/h；Gradient cooling is at 1100 DEG C, 1000 DEG C and 900 DEG C points
Room temperature is cooled to the furnace after not being incubated 1h, 1h and 2h, vacuum is 10-3pa.Embodiment 3,20-21 is differed only in：
The annealing temperature and annealing time in each stage are differed in annealing process, and first stage to the rate of temperature fall of second stage is
10 DEG C/h, the rate of temperature fall of second stage to phase III is 20 DEG C/h, and vacuum is 10-3pa；Specifically it is shown in Table 4.
Table 4 is the preparation technology of the cBN- High Speed Steel Composites of embodiment 3,18-21.
Embodiment 3,22-23 is differed only in：Quenching process is differed；Embodiment 3,24-25 is differed only in：Return
Fiery process is differed；Specifically it is shown in Table 5.
Table 5 is the preparation technology of the cBN- High Speed Steel Composites of embodiment 3,22-25.
Also it is carried out a 26-29, embodiment 3,26-29 is differed only in：The particle diameter of the cBN powder of use not phase
Together, wherein, embodiment 26 uses the cBN powder that particle diameter is 0.5 μm, and embodiment 27 uses the cBN powder that particle diameter is 12 μm,
Embodiment 28 uses the cBN powder that particle diameter is 20 μm, and embodiment 29 uses the cBN powder that particle diameter is 50 μm.
Also it is carried out a 30-32, embodiment 3,30-32 is differed only in：The particle diameter of the cBN powder of use not phase
Together, wherein, embodiment 30 uses mass ratio for 1:1 particle diameter is 5 μm and 0.5 μm of two kinds of cBN powder, and embodiment 31 is used
Be mass ratio be 1:1 particle diameter is 5 μm and 12 μm of two kinds of cBN powder, and it is 1 that embodiment 32 uses mass ratio:1 particle diameter
It is 5 μm and 20 μm of two kinds of cBN powder.
In order to verify beneficial effects of the present invention, to the cBN- high-speed steel composite woods obtained by above-described embodiment 1-32 preparations
Sintered material hardness (referring to the hardness number of material after densification sintering, unit is HRA), the heat treatment state hardness of material are (after referring to temper
The hardness number of material, unit is HRC), heat treatment state three-point bending strength (tested after referring to temper using three-point bending strength
The rupture strength of the cBN- High Speed Steel Composites that machine is tested, unit is MPa) and consistency tested, test result is shown in
Table 6.Wherein, consistency >=98.5%；The shapes and sizes all same of pressed compact, is the cylindrical green compact of a diameter of 25mm,
Using the pressing pressure of 150MPa, the dwell time is 5min for the making of pressed compact；CBN powder used in embodiment 1-25
Particle diameter is 5 μm.
Table 6 is the mechanical property parameters of the cBN- High Speed Steel Composites of embodiment 1-32.
1-5 understands that the preferred composition of the high-speed steel precursor mixture of powders is in conjunction with the embodiments：Mass fraction is
3~15% Co powder, 32~75% Fe powder, 20~50% metal carbides powder, 0~2% C powder, still more preferably
Composition be：Mass fraction is 7~11% Co powder, 50~64% Fe powder, 25~39% metal carbides powder, 0~2%
C powder.The preferred composition of corresponding cBN- High Speed Steel Composites is：Mass fraction be 1~30% cBN, 2.7~
13.5% Co, 1.7~5.4% C, 14~45% metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race,
40.6~67.5% Fe, composition still more preferably is：Mass fraction be 5~20% cBN, 6.3~9.9% Co,
1.7~5.4% C, 20.7~31.5% metal, 45~57.6% selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race
Fe.Wherein, the SEM photograph of the cBN- High Speed Steel Composites of embodiment 2 is shown in Fig. 1, the cBN- high-speed steel composite woods of embodiment 3
The SEM photograph of material is shown in Fig. 2, and the SEM photograph of the cBN- High Speed Steel Composites of embodiment 4 is shown in Fig. 3.
In conjunction with the embodiments 3,6-9 understands, mass ratio W in carbide powder：Mo：Cr：V is preferably (8~12)：(3.5~
6.5)：(2.5~5.5)：(0~20), be still more preferably (9.5~10.5)：(4.5~5.5)：(3.5~4.5)：(7~
13)。
In conjunction with the embodiments 3,10-13 understands that cBN- High Speed Steel Composites precursor mixture of powders preferably includes quality
Fraction is 70~99% high-speed steel precursor mixture of powders, 1~30% cBN powder, still more preferably including quality point
Number is 80~95% high-speed steel precursor mixture of powders, 5~20% cBN powder.
In conjunction with the embodiments 3,14-15 understands that the preparation parameter of high-speed steel precursor powder mixture is preferably：Ratio of grinding media to material is
(4~6)：1, packing factor is 0.4~0.8, and ball milling speed is 20~30 turns/min, and Ball-milling Time is 24~48h；With reference to implementation
Example 3,16-17 understands that the preparation parameter of cBN- High Speed Steel Composites precursor powder mixtures is preferably：Ratio of grinding media to material is (0.5
~1.5)：1, packing factor is 0.4~0.8, and ball milling speed is 20~30 turns/min, and Ball-milling Time is 6~10h.
In conjunction with the embodiments 3,18-25 understands that the sintering temperature of preferred sintering densification process is 1150 DEG C, sintering time
It is 1h；The annealing temperature of the first stage of preferred annealing process is 930 DEG C, and annealing time is 0.5h, the annealing of second stage
Temperature is 750 DEG C, and annealing time is 1.5h, and the annealing temperature of phase III is 600 DEG C, and annealing time is 1.5h；Preferably quench
The hardening heat of the first stage of fiery process is 540 DEG C, and the cool time is 1.5m, and the hardening heat of second stage is 930 DEG C, is quenched
The fiery time is 0.5h, and the hardening heat of phase III is 1150 DEG C, and the cool time is 10min, and the hardening heat of fourth stage is
540 DEG C, the cool time is 1h, and the hardening heat in the 5th stage is 280 DEG C, and the cool time is 1h；Preferred tempering stage is returned
Fiery temperature is 580 DEG C, and tempering time is 2h, and times of tempering is 3 times.
In conjunction with the embodiments 3,26-29 understands that, when the particle diameter of cBN powder is 0.5~50 μm, corresponding cBN- high-speed steel is combined
Material is respectively provided with preferable hardness.In conjunction with the embodiments 3,26-32 understands that the cBN powder using two kinds of particle diameters is preparation-obtained
CBN- High Speed Steel Composites with only with a kind of cBN powder in two kinds of particle diameters compared with small particle prepare cBN- high-speed steel be combined
The performance of material is approached, when added in the cBN powder of greater particle size part compared with small particle cBN powder after, gained cBN- high-speed steel
The hardness of composite is obviously improved.Therefore, taking cost into account, it is preferred to use two kinds of cBN powder of particle diameter.
Claims (10)
1. the high-speed steel precursor mixture of powders of cBN- High Speed Steel Composites is prepared, it is characterised in that：Before the high-speed steel
Body mixture of powders including Co powder that mass fraction is 3~15%, 32~75% Fe powder, 20~50% selected from element week
Carbide powder, 0~2% C powder of the metal of the races of phase Biao 4, the 5th race and the 6th race.
2. the high-speed steel precursor mixture of powders of cBN- High Speed Steel Composites, its feature are prepared as claimed in claim 1
It is：The carbide powder of the metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race includes WC powder, Mo2C powder, Cr3C2
Powder and VC powder, mass ratio W in the carbide powder：Mo：Cr：V is (8~12)：(3.5~6.5)：(2.5~5.5)：(0~
20)。
3. the high-speed steel precursor mixture of powders of cBN- High Speed Steel Composites, its feature are prepared as claimed in claim 2
It is：The high-speed steel precursor mixture of powders includes Co powder, 50~64% Fe powder, 25 that mass fraction is 7~11%
Carbide powder, 0~2% C powder of~39% metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race；The carbonization
Mass ratio W in thing powder：Mo：Cr：V is (9.5~10.5)：(4.5~5.5)：(3.5~4.5)：(7~13).
4.cBN- High Speed Steel Composites, it is characterised in that：Including cBN, 2.7~13.5% that mass fraction is 1~30%
Co, 1.7~5.4% C, 14~45% metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race, 40.6~
67.5% Fe.
5. cBN- High Speed Steel Composites as claimed in claim 4, it is characterised in that：It is described selected from the race of the periodic table of elements the 4th,
The metal of the 5th race and the 6th race includes W, Mo, Cr and V, mass ratio W in the metal：Mo：Cr：V is (8~12)：(3.5~
6.5)：(2.5~5.5)：(0~20).
6. cBN- High Speed Steel Composites as claimed in claim 5, it is characterised in that：The cBN- High Speed Steel Composites bag
Include cBN, 6.3~9.9% Co, 1.7~5.4% C, 20.7~31.5% that mass fraction is 5~20% selected from element
Metal, 45~57.6% Fe of the race of periodic table the 4th, the 5th race and the 6th race；Mass ratio W in the metal：Mo：Cr：V is (9.5
~10.5)：(4.5~5.5)：(3.5~4.5)：(7~13).
7. cBN- High Speed Steel Composites as claimed in claim 4, it is characterised in that：In the cBN- High Speed Steel Composites
The average grain diameter of cBN is 0.5~50 μm；The cBN- High Speed Steel Composites include the different cBN of at least two particle diameters.
8. cBN- High Speed Steel Composites as claimed in claim 7, it is characterised in that：At least two particle diameter is different
The particle diameter of cBN is respectively selected from 0.5 μm, 5 μm, 12 μm, 20 μm, 50 μm.
The preparation method of 9.cBN- High Speed Steel Composites, the method including the step of be：
1) high-speed steel precursor powder mixture is prepared：It is including mass fraction according to the high-speed steel precursor mixture of powders
3~15% Co powder, 32~75% Fe powder, 20~50% metal selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race
Carbide powder, the proportioning of 0~2% C powder weigh raw material, then by various raw materials in ball mill with (4~6)：1 ball material
Than, the ball milling speed of 0.4~0.8 packing factor, 20~30 turns/min, the ball milling of 24~48h is carried out, that is, prepared at a high speed
Steel precursor powder mixture；
2) cBN- High Speed Steel Composites precursor powder mixtures are prepared：According to cBN- High Speed Steel Composites precursor powders
Claim containing the high-speed steel precursor powder mixture, the proportioning of 1~30% cBN powder that mass fraction is 70~99% in mixture
Take the high-speed steel precursor powder mixture and cBN powder, then by two kinds of raw materials in ball mill with (0.5~1.5)：1
Ratio of grinding media to material, 0.4~0.8 packing factor, the ball milling speed of 20~30 turns/min, carry out the ball milling of 6~10h, that is, prepare
CBN- High Speed Steel Composites precursor powder mixtures；
3) it is molded：CBN- High Speed Steel Composites precursor powder mixtures are made by pressed compact by hydraulic press；
4) vacuum-sintering densification is carried out to pressed compact：Sintering temperature is warming up to 1130 with the heating rate of 80~120 DEG C/h~
1170 DEG C and 0.5~1.5h is incubated, then using being come out of the stove after rate of temperature fall gradient cooling to the room temperature of 180~220 DEG C/h；
5) vacuum softening annealing：0.25~0.75h is incubated first at a temperature of 900~950 DEG C, then with 8~12 DEG C/h's
Rate of temperature fall is cooled to 700~800 DEG C and is incubated 1~2h, is then cooled to 550~650 with the rate of temperature fall of 18~22 DEG C/h
DEG C and be incubated 1~2h, then furnace cooling is to coming out of the stove after room temperature；
6) quench：First stage is to be put into the sintering furnace that temperature is 520~560 DEG C, is come out of the stove after insulation tmin, and second stage is to put
Enter the sintering furnace that temperature is 830~870 DEG C, come out of the stove after insulation tmin, the phase III is that to be put into temperature be 1130~1170 DEG C
Sintering furnace, comes out of the stove after 8~12min of insulation, and fourth stage is to be put into the sintering furnace that temperature is 520~560 DEG C, and insulation 0.5~
Come out of the stove after 1.5h, the 5th stage was to be put into the sintering furnace that temperature is 260~300 DEG C, come out of the stove after 0.5~1.5h of insulation, Ran Houkong
It is as cold as room temperature；Wherein, t=(1~2) * m, m are the effective dimensions of pressed compact, and unit is mm；
7) it is tempered：The sintering furnace that temperature is 560~600 DEG C is put into, is come out of the stove after insulation >=1h, be then air cooled to room temperature；Repeat 2
Obtain cBN- High Speed Steel Composites afterwards~5 times, it is 1~30% that the cBN- High Speed Steel Composites contain mass fraction
CBN, 2.7~13.5% Co, 1.7~5.4% C, 14~45% selected from the race of the periodic table of elements the 4th, the 5th race and the 6th race
Metal, 40.6~67.5% Fe.
10. the preparation method of cBN- High Speed Steel Composites as claimed in claim 9, it is characterised in that：It is described selected from element
The carbide powder of the metal of the race of periodic table the 4th, the 5th race and the 6th race includes WC powder, Mo2C powder, Cr3C2Powder and VC powder, the carbonization
Mass ratio W in thing powder：Mo：Cr：V is (8~12)：(3.5~6.5)：(2.5~5.5)：(0~20).
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| CN108642402A (en) * | 2018-06-04 | 2018-10-12 | 湘潭大学 | Novel aluminum nitride dispersion-strengtherning powder metallurgy aluminium high-speed steel and preparation method thereof |
| CN109518072A (en) * | 2018-10-12 | 2019-03-26 | 东莞市煜田新材料有限公司 | A kind of high vanadium alloy carbide additive and its preparation method, application |
| CN110273097A (en) * | 2019-06-28 | 2019-09-24 | 鞍钢股份有限公司 | VC/V10 powder high-speed steel composite material and preparation method thereof |
| CN113649583A (en) * | 2021-08-09 | 2021-11-16 | 天工爱和特钢有限公司 | Preparation method of high-speed steel powder metallurgy product |
| US11707784B2 (en) | 2019-10-15 | 2023-07-25 | King Fahd University Of Petroleum And Minerals | Spark plasma sintered cBN and Ni-cBN bearing steel |
| CN118926533A (en) * | 2024-07-24 | 2024-11-12 | 深圳职业技术大学 | A method for preparing internally cooled cutting tools based on additive manufacturing and sintering optimization |
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Application publication date: 20170531 |
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