CN102634790A - Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer and preparation method thereof - Google Patents
Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer and preparation method thereof Download PDFInfo
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- CN102634790A CN102634790A CN2012101356334A CN201210135633A CN102634790A CN 102634790 A CN102634790 A CN 102634790A CN 2012101356334 A CN2012101356334 A CN 2012101356334A CN 201210135633 A CN201210135633 A CN 201210135633A CN 102634790 A CN102634790 A CN 102634790A
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Abstract
The invention discloses an Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer and a preparation method thereof and belongs to the field of surface engineering. The anti-corrosion layer is the iron-rich Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer which is generated in situ by adopting laser treatment technology on pearlite heat-resistant steel. The anti-corrosion layer is prepared according to the method which comprises the following steps: firstly, performing oil-removing and de-rusting treatment on a pearlite heat-resistant steel substrate, and then forming the iron-rich Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer in situ on the pearlite heat-resistant steel substrate by titanium aluminum powder mixture through laser. By designing the iron-rich Fe-Ti and Fe-Al complex-phase intermetallic compound anti-corrosion layer by the invention, on one hand, the high-temperature corrosion resistance under high-temperature chloric oxidation condition is obviously increased in comparison with an aluminum-rich Fe-Al intermetallic compound anti-corrosion layer, on the other hand, a more effective anti-corrosion layer for resisting biomass ash high-temperature corrosion is supplied for solving the problem of serious high-temperature corrosion of a boiler overheat pipe.
Description
Technical field
The invention belongs to field of surface engineering technique, particularly a kind of Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer and preparation method thereof.
Background technology
Biomass power generation is one of important means and mode of development low-carbon economy and recycling economy.In order to improve the generating efficiency of biomass electric power plant, China produces and has moved the biomass boiler (540 ℃ of vapor temperatures, vapor pressure 9.2 MPa) of HTHP type.But along with the raising of steam parameter, biomass boiler superheater tube heavy corrosion problem has appearred.This is owing to contain the higher alkali metal muriate in biomass boiler incendiary yellow stalk and the grey stalk; In combustion processes, discharge chloride low-melting material; Cause the serious slagging scorification of superheating surface; Under the effect of lime-ash and flue gas, make superheater tube produce serious high temperature alkali metal chloride corrosion.
For the serious high temperature corrosion problem of superheater tube, the boiler mfr selects for use austenitic heat-resistance steel to make superheater tube usually.Although select for use the high austenitic heat-resistance steel of cost can improve the high temperature chlorine corrosion resistant performance of superheater tube to a certain extent; But the serious high temperature corrosion problem of superheater tube still happens occasionally; Even the biomass boiler that has operation less than just took place in 15 months superheater tube corrosion pipe explosion accident (Li Qing etc. generating set, 2009 (3): 214).Biomass boiler suphtr booster is not because the hot strength deficiency of suphtr tube steel but high temperature relate to due to the high temperature corrosion of chlorine environment.And that the characteristic of austenitic heat-resistance steel is a hot strength is higher, and high-temperature oxidation resistance is better, but the resistance to high temperature corrosion ability is general in chloride well-oxygenated environment.It is the effective way with raising boiler superheater tube high-temperature corrosion resistance life-span of better economy that pearlite type suphtr tube steel is carried out surface modification treatment.Boi1er tube is carried out the aluminizing pipe that aluminising processes has been used for coal-fired power station boiler water wall tube and superheater tube, its well anti-fiery side high temperature corrosion property obtained better economic benefits (Cai Zhigang, Xie Tao. thermal power generation, 1996, (1): 3).In the current aluminizing pipe aluminized coating be organized as the Fe-Al intermetallic compound, be mainly FeAl and Fe
2Al
5
Summary of the invention
The shortcoming that the present invention is directed to above-mentioned boiler overheating tube material has been carried out the improvement of novelty, has proposed a kind of Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer and preparation method thereof.
The invention provides a kind of Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer, wherein the ratio of aluminium element and titanium elements is 1:19 ~ 1:4, and this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.
The invention still further relates to the preparation method of above-mentioned Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer, these method concrete steps are following:
With granularity is 100 orders～200 orders, and the aluminium powder of purity >=99.5% is put into mixed powder machine with titanium valve and mixed 20 minutes, and wherein the content of aluminium powder is 5 wt%～20 wt%, and all the other are titanium valve.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3 mm, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.The anticorrosion layer thickness that makes is 300 μ m ~ 400 μ m.
Beneficial effect: the present invention is through the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of a kind of rich iron of design, and this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.One side is with respect to the Fe-Al intermetallic compound anticorrosion layer of rich aluminium; Relate in the well-oxygenated environment of chlorine at high temperature; Its high-temperature corrosion resistance performance has had and has significantly improved; For solving the serious high temperature corrosion problem of boiler overheating pipe, a kind of anticorrosion layer of the more effective lime-ash of anti-biomass high temperature corrosion is provided on the other hand.
Description of drawings
Fig. 1 a ~ Fig. 1 e is respectively embodiment 1 ~ embodiment 5 and FeAl-Fe in the time of 600 ℃
2Al
5Oxidation kinetics curve comparison diagram.
Fig. 2 is the cross section backscattered electron composition picture of the anticorrosion layer of embodiment 1 preparation, and wherein the left side is a matrix, and the right side is a surface reforming layer.
Fig. 3 is the XRD figure spectrum of the anticorrosion layer of embodiment 2 preparations.
Embodiment
The invention provides a kind of Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer and preparation method thereof, the present invention is further specified below in conjunction with accompanying drawing and specific embodiment.
Embodiment 1
Take by weighing aluminium powder (granularity is 100 orders～200 orders, purity >=99.5%) 5 grams, titanium valve (granularity is 100 orders～200 orders, purity >=99.5%) 95 grams are put into and are mixed powder machine mixing 20 minutes.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3 mm, and control applies about 0.5 mm of bed thickness, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.The anticorrosion layer thickness that makes is 300 μ m ~ 400 μ m, sees Fig. 2.Be embedded in the biomass lime-ash behind 600 ℃ of high temperature oxidation and corrosion 214 h, its solidity to corrosion is FeAl-Fe
2Al
53.7 times of anticorrosion layer are seen Fig. 1 a.
Embodiment 2
Take by weighing aluminium powder (granularity is 100 orders～200 orders, purity >=99.5%) 10 grams, titanium valve (granularity is 100 orders～200 orders, purity >=99.5%) 90 grams are put into and are mixed powder machine mixing 20 minutes.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3 mm, and control applies about 0.5 mm of bed thickness, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.Anticorrosion layer thickness is 300 μ m ~ 400 μ m, and Fig. 3 is seen in the phase composite of anticorrosion layer, is embedded in the biomass lime-ash behind 600 ℃ of high temperature oxidation and corrosion 214 h, and its solidity to corrosion is FeAl-Fe
2Al
54.0 times of anticorrosion layer are seen Fig. 1 b.
Embodiment 3
Take by weighing aluminium powder (granularity is 100 orders～200 orders, purity >=99.5%) 20 grams, titanium valve (granularity is 100 orders～200 orders, purity >=99.5%) 80 grams are put into and are mixed powder machine mixing 20 minutes.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3mm, and control applies about 0.5 mm of bed thickness, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.Anticorrosion layer thickness is 300 μ m ~ 400 μ m, is embedded in the biomass lime-ash behind 600 ℃ of high temperature oxidation and corrosion 214 h, and its solidity to corrosion is FeAl-Fe
2Al
53.9 times of anticorrosion layer are seen Fig. 1 c.
Embodiment 4
Take by weighing aluminium powder (granularity is 100 orders～200 orders, purity >=99.5%) 15 grams, titanium valve (granularity is 100 orders～200 orders, purity >=99.5%) 85 grams are put into and are mixed powder machine mixing 20 minutes.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3 mm, and control applies about 0.5 mm of bed thickness, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.Anticorrosion layer thickness is 300 μ m ~ 400 μ m, is embedded in the biomass lime-ash behind 600 ℃ of high temperature oxidation and corrosion 214 h, and its solidity to corrosion is FeAl-Fe
2Al
54.2 times of anticorrosion layer are seen Fig. 1 d.
Embodiment 5
Take by weighing aluminium powder (granularity is 100 orders～200 orders, purity >=99.5%) 12 grams, titanium valve (granularity is 100 orders～200 orders, purity >=99.5%) 88 grams are put into and are mixed powder machine mixing 20 minutes.Powder mix is modulated into pasty state, and the geometrical dimension that is coated in oil removing, rust cleaning is on the 20 g pearlite heatproof steel matrixes of 100 mm * 200 mm * 3 mm, and control applies about 0.5 mm of bed thickness, and the coat oven dry is placed on the cladding worktable.The laser work head that employing links to each other with optical fiber is done horizontal uniform motion, workpiece fixed method; Directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction are generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING, this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.The concrete cladding parameter of LASER HEATING is: laser output power 500 W, and spot diameter 3 mm, laser frequency 10 Hz, pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%, shielding gas are argon gas, shield gas flow rate is 10 ml/s.Anticorrosion layer thickness is 300 μ m ~ 400 μ m, is embedded in the biomass lime-ash behind 600 ℃ of high temperature oxidation and corrosion 214 h, and its solidity to corrosion is FeAl+Fe
2Al
54.2 times of anticorrosion layer are seen Fig. 1 e.
Claims (6)
1. Fe-Ti and Fe-Al complex phase intermetallic compound anticorrosion layer, it is characterized in that: this anticorrosion layer is made up of the Fe-Ti and the Fe-Al complex phase intermetallic compound of rich iron, and wherein the ratio of aluminium element and titanium elements is 1:19 ~ 1:4.
2. Fe-Ti according to claim 1 and Fe-Al complex phase intermetallic compound anticorrosion layer, it is characterized in that: this anticorrosion layer is by the Fe of rich iron
2Ti and Fe
3Al complex phase intermetallic compound constitutes.
3. the preparation method of described Fe-Ti of claim 1 and Fe-Al complex phase intermetallic compound anticorrosion layer, it is characterized in that: these method concrete steps are following:
With granularity is 100 orders～200 orders; The aluminium powder of purity >=95% is put into mixed powder machine with titanium valve and was mixed 20 minutes; Wherein the content of aluminium powder is 5 wt%～20 wt% in the titanium aluminium mixed powder; All the other are titanium valve, and powder mix is modulated into pasty state, are coated on the pearlite heatproof steel matrix of oil removing, rust cleaning; Coat oven dry is placed on the cladding worktable, directly titanium aluminium mixed powder and pearlite heatproof steel matrix generation in-situ synthesized reaction is generated the Fe-Ti and the Fe-Al complex phase intermetallic compound anticorrosion layer of rich iron through LASER HEATING.
4. the preparation method of Fe-Ti according to claim 3 and Fe-Al complex phase intermetallic compound anticorrosion layer; It is characterized in that: the laser work head that said LASER HEATING process employing links to each other with optical fiber is done horizontal uniform motion, the workpiece fixed method prepares anticorrosion layer; The laser work head is done linear uniform motion at the x direction of principal axis, and the y direction of principal axis is done adjustable step motion.
5. the preparation method of Fe-Ti according to claim 3 and Fe-Al complex phase intermetallic compound anticorrosion layer is characterized in that: the concrete cladding parameter of said LASER HEATING is: laser output power 500 W, spot diameter 3 mm; Laser frequency 10 Hz; Pulsewidth 3.2 ms, laser beam flying speed 4 mm/s, overlapping rate 50%; Shielding gas is an argon gas, and shield gas flow rate is 10 ml/s.
6. the preparation method of Fe-Ti according to claim 3 and Fe-Al complex phase intermetallic compound anticorrosion layer is characterized in that: said anticorrosion layer thickness is 300 μ m ~ 400 μ m.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108326299A (en) * | 2017-01-20 | 2018-07-27 | 波音公司 | The method and its product of object are produced by the granular materials coated with metal material |
| CN111593345A (en) * | 2020-07-13 | 2020-08-28 | 中国人民解放军陆军装甲兵学院 | Composite powder and preparation method thereof, and anti-contact fatigue coating and preparation method thereof |
| WO2022111739A1 (en) * | 2020-11-30 | 2022-06-02 | 湖南金天铝业高科技股份有限公司 | Iron-aluminum alloy composite reinforced aluminum-based material, preparation method therefor and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03197632A (en) * | 1989-12-25 | 1991-08-29 | Nippon Steel Corp | Intermetallic compound tial-fe base alloy |
| US20020031603A1 (en) * | 2000-07-14 | 2002-03-14 | Jsr Corporation | Coating method by intermetallic compound |
| CN101994077A (en) * | 2010-10-27 | 2011-03-30 | 江苏科技大学 | High-temperature oxidation resisting intermetallic compound coating and preparation method thereof |
-
2012
- 2012-05-03 CN CN 201210135633 patent/CN102634790B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03197632A (en) * | 1989-12-25 | 1991-08-29 | Nippon Steel Corp | Intermetallic compound tial-fe base alloy |
| US20020031603A1 (en) * | 2000-07-14 | 2002-03-14 | Jsr Corporation | Coating method by intermetallic compound |
| CN101994077A (en) * | 2010-10-27 | 2011-03-30 | 江苏科技大学 | High-temperature oxidation resisting intermetallic compound coating and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| SU-MING ZHU ETAL: "Characterization of mechanically alloyed ternary Fe-Ti-Al powders", 《MATERIALS SCIENCE AND ENGINEERING: A》 * |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108326299A (en) * | 2017-01-20 | 2018-07-27 | 波音公司 | The method and its product of object are produced by the granular materials coated with metal material |
| CN108326299B (en) * | 2017-01-20 | 2021-04-16 | 波音公司 | Method of producing an article from particulate material coated with a metallic material and article thereof |
| US11045905B2 (en) | 2017-01-20 | 2021-06-29 | The Boeing Company | Method of manufacturing an object from granular material coated with a metallic material and a related article of manufacture |
| CN111593345A (en) * | 2020-07-13 | 2020-08-28 | 中国人民解放军陆军装甲兵学院 | Composite powder and preparation method thereof, and anti-contact fatigue coating and preparation method thereof |
| CN111593345B (en) * | 2020-07-13 | 2021-04-13 | 中国人民解放军陆军装甲兵学院 | Composite powder and preparation method thereof, and anti-contact fatigue coating and preparation method thereof |
| WO2022111739A1 (en) * | 2020-11-30 | 2022-06-02 | 湖南金天铝业高科技股份有限公司 | Iron-aluminum alloy composite reinforced aluminum-based material, preparation method therefor and application thereof |
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