CN105132824B - High rigidity does not ftracture laser cladding layer martensite iron(-)base powder and preparation method thereof - Google Patents
High rigidity does not ftracture laser cladding layer martensite iron(-)base powder and preparation method thereof Download PDFInfo
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- CN105132824B CN105132824B CN201510581192.4A CN201510581192A CN105132824B CN 105132824 B CN105132824 B CN 105132824B CN 201510581192 A CN201510581192 A CN 201510581192A CN 105132824 B CN105132824 B CN 105132824B
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Abstract
Laser cladding layer martensite iron(-)base powder and preparation method thereof the invention discloses high rigidity does not ftracture, according to mass percent, choose 16～17% Cr, 2.0～5.0% Ni, 0.05～0.15% B, 0.1～0.7% Si, 0.1～0.3% C, balance of Fe, by the alloy vacuum melting of mentioned component, aerosolization.The special martensite iron(-)base powder of laser melting coating of the present invention, cladding layer is obtained by rapid laser-shaping technique, average Rockwell hardness is 58.58HRC, the defect such as surface and section flawless and pore, and it is compressive stress that the Volumetric expansion produced using martensitic phase transformation makes laser cladding layer residual stress, effectively suppress the Initiation And Propagation of crackle, disclosure satisfy that the indehiscent use requirement of laser cladding layer high rigidity.
Description
Technical field
The invention belongs to laser remanufacturing technical field, it is related to a kind of high rigidity and does not ftracture laser cladding layer martensite iron-based
Alloy powder, the invention further relates to the preparation method of the powder.
Background technology
Laser melting and coating technique is surface modifying method emerging in recent years, prepares high rigidity cladding with laser melting and coating technique
Layer can greatly improve the service life of part, have a high potential in commercial Application.The existing nearly 40 years history of correlational study, it is relevant
Theory and tentative research it is a lot, but this technology does not obtain extensive promotion and application in the industrial production,
Main reason is that laser cladding layer easily ftractures, laser cladding forming part hardness is particularly evident when high.
At present, conventional cladding alloy powder is mainly fe-based self-fluxing alloy powder and self-fusible alloy powder of nickel-base,
, in design in order that fusing point is close proximity to eutectic point, the content of usual B, Si is higher for such powder, and the increase of B, Si element
Hard phase can be generated, so as to improve cladding layer hardness, causes plasticity to decline, increase cladding layer cracking behavior.The process of laser melting coating
In, under high energy laser beam irradiation, in autolyzed alloy powder and matrix flash melt and cooling procedure, due to molten coating and base
The difference of the thermal coefficient of expansion of body, therefore rate of cooling is incomplete same, contractility is also inconsistent, causes the remnants in molten coating
Stress effectively cannot discharge, and the composition such as element such as carbon, boron, silicon, nickel can form low in molten bath in self-fluxing alloyed powder
Melting eutectic thing is gathered on crystal boundary, and during crystallisation by cooling, cladding layer shrinks and produces pulling force, when acting on the residual of crystal boundary
Remaining tension is constantly gathered and is cracked when becoming greatly to the yield limit more than cladding layer.
At present the method for control residual stress mainly have reduction thermograde, using micro- forging, ultrasonic activation etc., but this
A little method complex process, can not effectively prevent the generation of crackle.It is adjustment Ni, B, Si etc. to solve one of approach of problem of Cracking
The content strain induced martensite phase transformation of alloying element, due to different mutually with different density and different lattice types, thus
With different specific volumes, when austenite is changed into martensite, its specific volume will increase to 0.127- by 0.123-0.125
0.131, cause its stress state to change, answer so as to offsetting residual tension or residual tension being transformed into residual pressure
Power.Ferrous alloy has huge price advantage relative to nickel-base alloy, therefore considers price factor, currently solves high rigidity
The feasible method of cladding layer problem of Cracking is to develop laser melting coating special-purpose iron-base alloy powder.
The content of the invention
It is an object of the invention to provide a kind of high rigidity does not ftracture, laser cladding layer martensite iron(-)base powder, solves
Problems of the prior art, can prevent cracking in laser melting and coating process.
It is a further object of the present invention to provide the preparation method of above-mentioned iron(-)base powder.
The technical solution adopted in the present invention is, a kind of high rigidity does not ftracture laser cladding layer martensite fe-based alloy powder
End, according to mass percent, is made up of following raw material：It is that 2.0～5.0%, B is 0.05～0.15% that Cr is 16～17%, Ni,
It is 0.1～0.3% that Si is 0.1～0.7%, C, balance of Fe.
Another technical scheme of the present invention is, a kind of high rigidity does not ftracture laser cladding layer martensite ferrous alloy
The preparation method of powder, specifically follows the steps below：According to mass percent, 16～17% Cr chosen, 2.0～
5.0% Ni, 0.05～0.15% B, 0.1～0.7% Si, 0.1～0.3% C, balance of Fe, by mentioned component
Alloy vacuum melting, aerosolization.
The invention has the beneficial effects as follows special martensite iron(-)base powder is not ftractureed as raw material with high rigidity, using organic
Thing double-coating technique, by rapid laser-shaping technique obtain cladding layer, average Rockwell hardness be 58.58HRC, surface and cut
The defect such as face flawless and pore, and the Volumetric expansion produced using martensitic phase transformation makes laser cladding layer residual stress
For compressive stress, effectively suppress the Initiation And Propagation of crackle, disclosure satisfy that the indehiscent use requirement of high rigidity.
Description of the drawings
The comparison diagram of Fig. 1 b after the front Fig. 1 a of pattern cutting of Fig. 1 special-purpose iron-base alloy composite powder cladding layers and cutting.
Fig. 2 is surface topography after cladding layer polishing, wherein, Fig. 2 a are exterior view, and Fig. 2 b are sectional view.
Fig. 3 is laser fast shaping stretching mechanical assay maps.
Specific embodiment
The present invention is described in detail with reference to the accompanying drawings and detailed description.
A kind of high rigidity does not ftracture laser cladding layer iron(-)base powder, and according to mass percent, alloy is by following element
Composition：Ours test result indicate that：When in alloy, chromium content is less than 15%, can cause to produce during follow-up cladding
Significantly surface oxidation, is decreased obviously the quality of laser cladding layer；When nickel content is more than 7%, laser cladding layer occur compared with
Many austenite phases, surface residual stress are tension, the trend for having cracking；When Boron contents higher than 0.15%, carbon content are higher than
When 0.3%, the fragility of laser cladding layer is significantly increased, and its comprehensive mechanical performance is decreased obviously.Consider the factor of each side,
This programme adopts low-carbon (LC), Gao Ge, a small amount of boron, low nickel martensite type iron-based rustless steel.Ju Ti Pei Fang is as follows：
Cr be 16～17%, Ni be 2.0～5.0%, B be 0.05～0.15%, Si be 0.1～0.7%, C be 0.1～
0.3%, balance of Fe.
Principle：, to make fusing point near eutectic point, B, Si containing high level are first for conventional self-fluxing nature iron(-)base powder
Element, and the increase of B, Si element can generate hard phase, so as to improve cladding layer hardness, cause plasticity to decline, and increase cladding layer and open
Fragility.Austenite can increase to volume during martensite transfor mation, can pass through to adjust the content induction of the alloying elements such as Ni, B, Si
Martensitic phase transformation, offsets residual tension or residual tension is transformed into residual compressive stress, so as to be prevented effectively from crackle
Produce.
A kind of high rigidity does not ftracture the preparation method of laser cladding layer iron(-)base powder, specifically enters according to following steps
OK：
According to mass percent, choose 16～17% Cr, 2.0～5.0% Ni, 0.05～0.15% B, 0.1～
0.7% Si, 0.1～0.3% C, balance of Fe.By the alloy vacuum melting of mentioned component, aerosolization.
The high rigidity of the present invention does not ftracture laser cladding layer iron(-)base powder, protects laser using water-cooled air curtain air flue
Lateral powder-feeding nozzle device：With 5KW crossing current CO2Laser instrument, by the base material Q235 of the 110mm × 45mm of blasting treatment × 15mm
Steel plate is put on laboratory bench, adjusts the nozzle of laser instrument and the distance of base material, using lateral synchronous powder feeding system method, base material by
Numerical control table, NC table drives.By alloy powder cladding in substrate surface, cambium layer size is the molten of long 90mm × wide 40mm × thickness 3mm
Coating.Laser processing technique parameter is：Laser power is 2200W-2500W, and spot diameter is 3-5mm, and scanning speed is 5-
7mm/s, powder feed rate are 5-7g/min, and overlapping fraction is 0.5-0.7, and protective gas is argon.High-quality, height can be obtained
The laser cladding layer of hardness.
1. high rigidity does not ftracture the morphology analysis of special-purpose iron-base alloy composite powder cladding layer：
Laser forming part is cut with base material faying face along cladding layer using wire cutting, obtain pattern such as Fig. 1 of cladding layer
It is shown.From figure 1 it appears that the sagging intermediate projections in cladding layer two ends, it is possible to determine that the residual stress suffered by cladding layer is pressure
Stress, Jing measurement cladding layer length is 92mm, and angularity is 0.8mm, and residual compressive stress is 530MPa.
From Fig. 2, surface and section can be seen that special metals powder melting layer surface does not have the defects such as crackle pore, into
Shape part quality is good, meets requirement of not ftractureing.
2. high rigidity does not ftracture laser cladding layer iron(-)base powder cladding layer hardness test：
This experiment measures its superficial Rockwell microhardness using the full Rockwell apparatuses of TH320, and experiment is carried out at room temperature, real
It is 150Kg to test power, and the dwell time is 6s.Take 10 points to measure, as it can be seen from table 1 the average Rockwell hardness of coating is
58.58HRC (maximum hardness is 62.5HRC, and hardness minima is 54.9HRC), meets high rigidity requirement.
1 coating Rockwell hardness of table
3. high rigidity do not ftracture laser cladding layer iron(-)base powder cladding layer tensile strength test：
Sample is processed into into Fig. 3 shapes, dimensional units mm in figure, using PWS-E100 type electro-hydraulic servo sound universal tests
Machine, if draw speed is 0.1mm/min, carries out static tensile test to sample.Measurement result shows, average before sample annealing
Tensile strength 1847MPa (ultimate tensile strength is 1867MPa, and minimum tensile strength is 1828MPa), after 600 DEG C of annealing of sample
Average tensile strength be 1460MPa (ultimate tensile strength is 1488MPa, and minimum tensile strength is 1424MPa), illustrate shape
Part stable mechanical property.
In sum, iron(-)base powder laser cladding layer of the invention does not have the defects such as pore and slag inclusion, martensitic phase
The cladding layer residual compressive stress for becoming induction effectively suppresses the generation of crackle, and drip molding total quality is good, and intensity and hardness are high,
Comprehensive mechanical property is good.
Embodiment 1
According to mass percent, 16% Cr, 2.0% Ni, 0.05% B, 0.1% Si, 0.1% C are chosen, it is remaining
Measure as Fe.By the alloy vacuum melting of mentioned component, aerosolization.
Embodiment 2
According to mass percent, 17% Cr, 5.0% Ni, 0.15% B, 0.7% Si, 0.3% C are chosen, it is remaining
Measure as Fe.By the alloy vacuum melting of mentioned component, aerosolization.
Embodiment 3
According to mass percent, 16.5% Cr, 3% Ni, 0.1% B, 0.5% Si, 0.2% C are chosen, it is remaining
Measure as Fe.By the alloy vacuum melting of mentioned component, aerosolization.
Embodiment 4
According to mass percent, 16.7% Cr, 4% Ni, 0.08% B, 0.4% Si, 0.15% C are chosen,
Balance of Fe.By the alloy vacuum melting of mentioned component, aerosolization.
Claims (1)
1. high rigidity does not ftracture the preparation method of laser cladding layer martensite iron(-)base powder, it is characterised in that specifically according to
Following steps are carried out：According to mass percent, 16～17% Cr, 4.0～5.0% Ni, 0.05～0.15% B are chosen,
0.1～0.7% Si, 0.1～0.3% C, balance of Fe, by the alloy vacuum melting of mentioned component, aerosolization.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106555127A (en) * | 2016-11-30 | 2017-04-05 | 沈阳大陆激光工程技术有限公司 | A kind of iron(-)base powder that high-speed railway switch platen is manufactured for laser |
| CN107937909A (en) * | 2017-12-22 | 2018-04-20 | 北京工业大学 | A kind of laser melting coating Fe bases composite powder and restorative procedure for being used for sufficient roller reparation |
| CN108356263B (en) * | 2018-04-28 | 2019-09-24 | 苏州大学 | Laser gain material manufacture heat-resisting steel alloy powder of novel martensitic and preparation method thereof |
| CN108823565B (en) * | 2018-07-24 | 2020-05-29 | 南华大学 | Silicon-aluminum-vanadium-stable iron-based alloy powder for low-carbon micro-boron high-strength plastic martensite laser cladding layer and preparation and cladding methods |
| CN109234729A (en) * | 2018-11-01 | 2019-01-18 | 马鞍山市申马机械制造有限公司 | A kind of laser cladding powder |
| CN109371336B (en) * | 2018-12-10 | 2020-11-10 | 南华大学 | Preparation method of ultrahigh-strength and toughness forming layer |
| CN111607790A (en) * | 2020-06-12 | 2020-09-01 | 兰州理工大学白银新材料研究院 | Cladding agent for laser cladding and preparation method and application thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101054668A (en) * | 2007-05-17 | 2007-10-17 | 贵州光谷海泰激光技术有限公司 | Alloy powder for repairing engine member abandonment die by laser, application method and application thereof |
| CN101974724A (en) * | 2010-11-24 | 2011-02-16 | 上海交通大学 | Iron-based alloy powder for high strength and toughness laser deposited coating |
| CN103695900A (en) * | 2013-12-27 | 2014-04-02 | 中国科学院半导体研究所 | Preparation method for wear-resisting corrosion-resisting rod piece |
| CN104480462A (en) * | 2014-12-12 | 2015-04-01 | 南京理工大学 | Iron-based amorphous coating and laser preparation method thereof |
-
2015
- 2015-09-14 CN CN201510581192.4A patent/CN105132824B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101054668A (en) * | 2007-05-17 | 2007-10-17 | 贵州光谷海泰激光技术有限公司 | Alloy powder for repairing engine member abandonment die by laser, application method and application thereof |
| CN101974724A (en) * | 2010-11-24 | 2011-02-16 | 上海交通大学 | Iron-based alloy powder for high strength and toughness laser deposited coating |
| CN103695900A (en) * | 2013-12-27 | 2014-04-02 | 中国科学院半导体研究所 | Preparation method for wear-resisting corrosion-resisting rod piece |
| CN104480462A (en) * | 2014-12-12 | 2015-04-01 | 南京理工大学 | Iron-based amorphous coating and laser preparation method thereof |
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