CN106756584A - Iron base composite material and preparation method thereof - Google Patents
Iron base composite material and preparation method thereof Download PDFInfo
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- CN106756584A CN106756584A CN201611100828.XA CN201611100828A CN106756584A CN 106756584 A CN106756584 A CN 106756584A CN 201611100828 A CN201611100828 A CN 201611100828A CN 106756584 A CN106756584 A CN 106756584A
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- composite material
- iron base
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
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- 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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
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- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Powder Metallurgy (AREA)
Abstract
The present invention relates to a kind of iron base composite material, the enhancing of iron base composite material is mutually the NbC particles generated by Nb and C atoms reaction in-situ, nitrogen treatment is carried out to iron base composite material surface and forms Nb (C, N) particulates reinforcements, iron base composite material enhancing phase volume fraction is 26~43%；And disclose the specific preparation method of iron base composite material.The beneficial effects of the invention are as follows：The enhanced iron base composite materials of fabricated in situ NbC, and nitrogen treatment is carried out, generating a kind of Nb (C, N) solid solution in material surface strengthens distribution gradient between phase, with center portion NbC reinforcements；Because the enhancing of composite is mutually in-situ reactive synthesis, enhancing is reaction generation with basal body interface, does not have pollution problem, the composite has high anti-wear performance, especially surface property is more excellent, and the preparation process is simple of composite, production cost is relatively low.
Description
Technical field
The present invention relates to a kind of iron base composite material and preparation method thereof.
Background technology
Iron base composite material is high due to low cost, performance, can need to change enhancing mutually and matrix according to different, is mesh
It is preceding to develop metal-base composites faster.The preparation method of traditional composite is more, wherein having casting, high temperature from climing
Prolong method, powder metallurgic method etc., the forming method according to enhancing phase has additional enhancing phase method and fabricated in situ enhancing phase method.Additional increasing
Qiang Xiangfa has the interface pollution of larger drawback, particle and matrix, and matrix is poor with the adhesion of enhancing phase；Particle divides in the base
Cloth uniformity is poor, and the percent by volume for strengthening phase is restricted.Fabricated in situ enhancing phase method has obvious advantage, but at present
Casting can not reach volume fraction higher, wearability is restricted, and powder metallurgic method can prepare higher volumes point
The composite of number enhancing phase, while enhancing is mutually generated in-situ, the combination interface with matrix is clean.
At present, the enhancing of iron base composite material is mutually concentrated mainly on the carbide scope such as TiC, VC, WC, and Nb is a kind of pole
Good carbide former, while Nb and N also have very strong adhesion, can generate NbN, be also to strengthen phase well, and
NbC and NbN are sodium chloride face-centered cubic crystal structure, can mutually form Nb (C, N) carbonitride solid solution, this solid solution
The wearability of the enhanced iron base composite material of body has more than single carbide or nitride as the composite of enhancing phase
Plus excellent anti-wear performance, the service life of part can be greatly improved.And prepare the overall enhanced iron-based composite woods of Nb (C, N)
Material difficulty is higher, because the carbonization of Nb and nitridation reaction speed are different, reaction temperature is also inconsistent, prepares entirety Nb (C, N)
Enhanced iron base composite material technology difficulty is big.Therefore the invention is intended to prepare a kind of NbC using powder metallurgy in-situ synthesis
Enhanced iron base composite material, is then carried out at nitridation at relatively low temperature to the composite after sintering densification
Reason, makes Nb (C, N) solid solution enhancing phase that a kind of hardness of Surface Creation is higher, and this surface has answering for Nb (C, N) enhancing phases
Condensation material can greatly improve the wearability of composite material surface, and material center portion NbC enhancings mutually still have good wearability,
By surface to center portion Nb (C, N) and NbC distribution gradients.
The content of the invention
The technical problem to be solved in the present invention is：Based on above mentioned problem, the present invention provide a kind of iron base composite material and its
Preparation method.
The present invention solves a technical scheme being used of its technical problem：A kind of iron base composite material, iron-based is combined
The enhancing of material is mutually the NbC particles generated by Nb and C atoms reaction in-situ, and the via nitride treatment of iron base composite material surface is formed
Nb (C, N) solid solution strengthens phase, and iron base composite material enhancing phase volume fraction is 26~43%, is calculated in mass percent, iron-based
Composite contains 23~38% Nb and 3~5% C.
The preparation method of iron base composite material, comprises the following steps：
(1) iron powder, ferro-niobium powder and graphite powder are mixed, is added in ball grinder, add abrading-ball, added in ball grinder anhydrous
Alcohol covers mixed-powder；
(2) ball milling is carried out in ball mill, the rotating speed of ball mill is 150~250r/min, and Ball-milling Time is 24h；
(3) the good powder of ball milling is well mixed with binding agent, sieving, and part pressed compact, compacting pressure are pressed into a press
Power is 350~400Mpa, and the dwell time is 30~60s；
(4) the part pressed compact that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 with the speed of 10 DEG C/min
DEG C, 30min is incubated, 1050 DEG C then are warmed up to the speed of 10 DEG C/min, 100min is incubated, it is finally heated to final temperature
1380~1420 DEG C, it is incubated 60~90min；
(5) 700~900 DEG C are cooled to, nitrogen is passed through, pressure is 0.25~0.30Mpa, is incubated 6~12h, makes surface NbC
Particle nitridation generation Nb (C, N), is obtained iron base composite material.
Further, in step (1) mass fraction of ferro-niobium powder and graphite powder be respectively 44.8~74.0% and 3.0~
5.0%, wherein Nb are 1 with the atomic ratio of C:1, one or two in mixed-powder in addition molybdenum-iron powder, ferrochrome powder are to matrix
Carry out alloying.
Further, binding agent is paraffin in step (3).
The beneficial effects of the invention are as follows：The enhanced iron base composite materials of fabricated in situ NbC, and nitrogen treatment is carried out, multiple
A kind of Surface Creation Nb (C, N) solid solution of condensation material part strengthens between phase, with center portion NbC reinforcements in a kind of gradient point
Cloth, between there is no obvious interface；Because the enhancing of composite is mutually in-situ reactive synthesis, strengthen the interface with matrix
It is reaction generation, does not have pollution problem, the composite has high anti-wear performance, and especially surface property is more excellent
Different, but preparation process is simple, production cost is relatively low.
Specific embodiment
Presently in connection with specific embodiment, the invention will be further described, and following examples are intended to illustrate rather than
Limitation of the invention further.
Embodiment 1
Step 1：Powder prepares
Powder composition：
Ferro-niobium powder：51.3%Nb
Graphite powder：99.9%C
Molybdenum-iron powder：59.4%Mo
Ferrochrome powder：56.2%Cr
Iron powder：98.5%Fe
Step 2：Ball milling is carried out in ball mill, Ball-milling Time is 24h, and the rotating speed of ball mill is 200r/min.
Step 3：The good powder of ball milling mixes with paraffin, then sieves, and part pressed compact, compacting pressure are pressed into a press
Power is 360MPa, dwell time 30s.
Step 4：The part that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 with the speed of 10 DEG C/min
DEG C, 30min is incubated, binding agent is decomposed and is discharged, 1050 DEG C then are warmed up to the speed of 10 DEG C/min, 100min is incubated, allow
Reaction in-situ is fully carried out, finally heated to 1380 DEG C of final temperature, is incubated 60min, sintering densification.
Step 5：750 DEG C are cooled to after sintering densification, nitrogen is passed through, pressure is 0.25Mpa, be incubated 6h so that sintering
Fine and close piece surface nitridation, makes surface NbC particles nitridation generation Nb (C, N), is obtained composite, the composite of system
Grain enhancing phase volume fraction is 26%, the case hardness HRA78 of composite, and wear test relative wear rate is Quenched 45 Steel
1.56 times.
Embodiment 2
Step 1：Powder prepares
| Composition | Granularity | Mass percent |
| Ferro-niobium powder | ≤50um | 63.9 |
| Graphite powder | ≤5um | 4.2 |
| Molybdenum-iron powder | ≤70um | 1.0 |
| Ferrochrome powder | ≤50um | 1.0 |
| Iron powder | ≤20um | 29.9 |
Step 2：Ball milling is carried out in ball mill, Ball-milling Time is 24h, and the rotating speed of ball mill is 200r/min.
Step 3：The good powder of ball milling mixes with paraffin, then sieves, and part pressed compact, compacting pressure are pressed into a press
Power is 360MPa, dwell time 30s.
Step 4：The part that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 with the speed of 10 DEG C/min
DEG C, 30min is incubated, binding agent is decomposed and is discharged, 1050 DEG C then are warmed up to the speed of 10 DEG C/min, 100min is incubated, allow
Reaction in-situ is fully carried out, finally heated to 1380 DEG C of final temperature, is incubated 60min, sintering densification.
Step 5：750 DEG C are cooled to after sintering densification, nitrogen is passed through, pressure is 0.25Mpa, be incubated 6h so that sintering
Fine and close piece surface nitridation, makes surface NbC particles nitridation generation Nb (C, N), is obtained composite, the composite of system
Grain enhancing phase volume fraction is 37%, the case hardness HRA79.5 of composite, and wear test relative wear rate is Quenched 45 Steel
1.94 times.
Embodiment 3
Step 1：Powder prepares
| Composition | Granularity | Mass percent |
| Ferro-niobium powder | ≤50um | 63.9 |
| Graphite powder | ≤5um | 4.2 |
| Molybdenum-iron powder | ≤70um | 1.0 |
| Ferrochrome powder | ≤50um | 1.0 |
| Iron powder | ≤20um | 29.9 |
Step 2：Ball milling is carried out in ball mill, Ball-milling Time is 24h, and the rotating speed of ball mill is 200r/min.
Step 3：The good powder of ball milling mixes with paraffin, then sieves, and part pressed compact, compacting pressure are pressed into a press
Power is 360MPa, dwell time 30s.
Step 4：The part that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 with the speed of 10 DEG C/min
DEG C, 30min is incubated, binding agent is decomposed and is discharged, 1050 DEG C then are warmed up to the speed of 10 DEG C/min, 100min is incubated, allow
Reaction in-situ is fully carried out, finally heated to 1380 DEG C of final temperature, is incubated 60min, sintering densification.
Step 5：750 DEG C are cooled to after sintering densification, nitrogen is passed through, pressure is 0.25Mpa, be incubated 12h so that sintering
Fine and close piece surface nitridation, makes surface NbC particles nitridation generation Nb (C, N), is obtained composite, the composite of system
Grain enhancing phase volume fraction is 37%, composite material surface hardness HRA81, and wear test relative wear rate is Quenched 45 Steel
2.03 times.
Embodiment 4
Step 1：Powder prepares
| Composition | Granularity | Mass percent |
| Ferro-niobium powder | ≤50um | 74.0 |
| Graphite powder | ≤5um | 5.0 |
| Molybdenum-iron powder | ≤70um | 1.0 |
| Ferrochrome powder | ≤50um | 1.0 |
| Iron powder | ≤20um | 19.0 |
Step 2：Ball milling is carried out in ball mill, Ball-milling Time is 24h, and the rotating speed of ball mill is 200r/min.
Step 3：The good powder of ball milling mixes with paraffin, then sieves, and part pressed compact, compacting pressure are pressed into a press
Power is 360MPa, dwell time 30s.
Step 4：The part that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 with the speed of 10 DEG C/min
DEG C, 30min is incubated, binding agent is decomposed and is discharged, 1050 DEG C then are warmed up to the speed of 10 DEG C/min, 100min is incubated, allow
Reaction in-situ is fully carried out, finally heated to 1400 DEG C of final temperature, is incubated 60min, sintering densification.
Step 5：750 DEG C are cooled to after sintering densification, nitrogen is passed through, pressure is 0.25Mpa, be incubated 6h so that sintering
Fine and close piece surface nitridation, makes surface NbC particles nitridation generation Nb (C, N), is obtained composite, the composite of system
Grain enhancing phase volume fraction is 43%, the case hardness HRA83 of composite, and wear test relative wear rate is Quenched 45 Steel
2.52 times.
With above-mentioned according to desirable embodiment of the invention as enlightenment, by above-mentioned description, relevant staff is complete
Various changes and amendments can be carried out without departing from the scope of the technological thought of the present invention' entirely.The technology of this invention
Property scope is not limited to the content on specification, it is necessary to its technical scope is determined according to right.
Claims (4)
1. a kind of iron base composite material, it is characterized in that：The enhancing of described iron base composite material is mutually in situ anti-by Nb and C atoms
The NbC particles that should be generated, iron base composite material surface via nitride treatment forms Nb (C, N) solid solution enhancing phase, iron-based composite wood
Material enhancing phase volume fraction be 26~43%, be calculated in mass percent, iron base composite material contain 23~38% Nb and 3~
5% C.
2. the preparation method of the iron base composite material described in claim 1, it is characterized in that：Comprise the following steps：
(1) iron powder, ferro-niobium powder and graphite powder are mixed, is added in ball grinder, add abrading-ball, absolute alcohol is added in ball grinder
Covering mixed-powder；
(2) ball milling is carried out in ball mill, the rotating speed of ball mill is 150~250min, and Ball-milling Time is 24h；
(3) powder after ball milling is well mixed with binding agent, sieving, and part pressed compact is pressed into a press, and pressing pressure is
350~400Mpa, the dwell time is 30~60s；
(4) the part pressed compact that will be suppressed is sintered in being put into vacuum sintering furnace, is first heated to 550 DEG C with the speed of 10 DEG C/min,
Insulation 30min, is then warmed up to 1050 DEG C with the speed of 10 DEG C/min, is incubated 100min, finally heated to final temperature 1380
~1420 DEG C, it is incubated 60~90min；
(5) 700~900 DEG C are cooled to, nitrogen is passed through, pressure is 0.25~0.30Mpa, is incubated 6~12h, makes surface NbC particles
Nitridation generation Nb (C, N), is obtained iron base composite material.
3. the preparation method of iron base composite material according to claim 2, it is characterized in that：Ferro-niobium in described step (1)
The mass fraction of powder and graphite powder is respectively 44.8~74.0% and 3.0~5.0%, and the atomic ratio of wherein Nb and C is 1:1, mix
One or two in conjunction powder in addition molybdenum-iron powder, ferrochrome powder carry out alloying to matrix.
4. the preparation method of iron base composite material according to claim 2, it is characterized in that：Bonded in described step (3)
Agent is paraffin.
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| CN201611100828.XA CN106756584B (en) | 2016-12-05 | 2016-12-05 | Iron base composite material and preparation method thereof |
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| CN201611100828.XA CN106756584B (en) | 2016-12-05 | 2016-12-05 | Iron base composite material and preparation method thereof |
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| CN106756584B CN106756584B (en) | 2018-07-20 |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107812956A (en) * | 2017-09-19 | 2018-03-20 | 南京航空航天大学 | A kind of composite powder preparation method and equipment for directly generating FeN enhancing phases |
| CN111876776A (en) * | 2020-08-10 | 2020-11-03 | 湖南人文科技学院 | NbC-reinforced nanocrystalline wear-resistant coating with hardness gradient and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102134677A (en) * | 2010-12-31 | 2011-07-27 | 南车戚墅堰机车车辆工艺研究所有限公司 | Iron-based composite material and preparation method thereof |
| CN105671411A (en) * | 2016-01-24 | 2016-06-15 | 中南大学 | Carbide-reinforced iron base composite material and powder metallurgy in-situ synthesis method thereof |
-
2016
- 2016-12-05 CN CN201611100828.XA patent/CN106756584B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102134677A (en) * | 2010-12-31 | 2011-07-27 | 南车戚墅堰机车车辆工艺研究所有限公司 | Iron-based composite material and preparation method thereof |
| CN105671411A (en) * | 2016-01-24 | 2016-06-15 | 中南大学 | Carbide-reinforced iron base composite material and powder metallurgy in-situ synthesis method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 鹿云等: "氮化处理粉末烧结材料耐磨性研究", 《农业机械学报》 * |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107812956A (en) * | 2017-09-19 | 2018-03-20 | 南京航空航天大学 | A kind of composite powder preparation method and equipment for directly generating FeN enhancing phases |
| CN107812956B (en) * | 2017-09-19 | 2019-07-30 | 南京航空航天大学 | A kind of composite powder preparation method and equipment directly generating FeN reinforced phase |
| CN111876776A (en) * | 2020-08-10 | 2020-11-03 | 湖南人文科技学院 | NbC-reinforced nanocrystalline wear-resistant coating with hardness gradient and preparation method thereof |
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| CN106756584B (en) | 2018-07-20 |
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