CN103710656A - Deformation machining process for nickel based alloys and iron nickel based alloys - Google Patents
Deformation machining process for nickel based alloys and iron nickel based alloys Download PDFInfo
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Abstract
The invention discloses a deformation machining process for nickel based alloys and iron nickel based alloys, and is used for solving the technical problems that the deformation machining of the nickel based alloys and the iron nickel based alloys in a solid solution state lowers the amount of crystal boundary carbide precipitation of materials in subsequent aging or serving process, thereby reducing the endurance strength, and the nickel based alloys and the iron nickel based alloys are low in plasticity, high in strength, difficult to deform and easy to crack when being subjected to deformation machining in an aging state. The process is technically characterized in that the nickel based alloys and the iron nickel based alloys subjected to solid solution treatment are subjected to one relatively-high-temperature heat treatment, carbides are precipitated near a crystal boundary firstly and simultaneously the precipitation of intracrystalline gamma' or gamma'' phases is reduced, then the obtained objects are subjected to deformation machining until the objects reach the required shape and size of parts, and finally, the obtained products are subjected to aging treatment, so that both the process properties of materials in the stage of deformation machining are ensured, and the final endurance strength of products is ensured.
Description
Technical field
The present invention relates to a kind of alloy deformation complete processing, particularly relate to the deformation processing technique of a kind of nickel-base alloy and iron nickel base alloy.
Background technology
Along with the attention to environment protection in the world, thermal power industry faces increasing CO
2the pressure of the pollution reductions such as greenhouse gases and SOx, NOx, the market competition that thermal power industry faces simultaneously is also being increasingly sharpened, and this all requires power plant further to reduce cost of electricity-generating.The effective ways that address these problems are exactly the thermo-efficiency that improves thermal power generation unit, and the steam parameter that improves unit is one of effective way of improving thermo-efficiency.Historical fuel-burning power plant successively from low pressure, pressure, high pressure, ultra-high voltage, subcritical, overcritically develop into current ultra supercritical parameter, current 600 ℃ of grade ultra supercritical power generation technology in Chinas are substantially ripe at home and abroad.
In order to pursue higher generating efficiency, people have proposed vapor temperature further to bring up to the research and development plan of 700 ℃ and above advanced ultra supercritical power generation technology in China.Because vapor temperature increases substantially, parts to some high temperature section of unit, as High-temperature Superheater In A Boiler, high temperature reheater, header and pipeline etc., traditional iron-based high temperature steel intensity and corrosion resistance etc. can not meet requirement, need to adopt that creep rupture strength is higher, erosion resistance can better Ni-based or Fe Ni matrix high temperature alloy.
Ni-based and iron nickel base alloy solid solution is divided into solution strengthening type alloy and the large class of precipitation strength type alloy two by schedule of reinforcement.Solution strengthening type alloy is to take the alloy that solution strengthening is main strengthening mechanism, by adding the element different from matrix metal atomic size (chromium, tungsten, molybdenum etc.) to cause the distortion of matrix metal dot matrix, add and can reduce the element (as cobalt) of alloy substrate stacking fault energy and add the element (tungsten, molybdenum etc.) that can slow down matrix element rate of diffusion, to strengthen matrix.
Precipitation strength or claim that ageing strengthening alloy is to take the alloy that precipitation hardening is main strengthening mechanism, by solid solution and ageing treatment, from supersaturated solid solution, separate out second-phase (γ ', γ ", carbide etc.), with reinforced alloys.
Ni-based or iron nickel base alloy for advanced ultra supercritical power generation unit, due to the requirement to parts high temperature long service, main candidate material be take precipitation strengthening alloy as main, as 263 alloys, 625 alloys, Inconel740H and Inconel740 alloy, Haynes282 alloy etc.Even if the part adopting classifies as the alloy of solution strengthening type, as 617 alloys, 617B(617mod.) alloy, thermal treatment or under arms also can carbide precipitate in process and γ ' wait precipitated phase." be mainly distributed in crystal grain inside, because its particle is little, quantity is many, and matrix is played to important strengthening effect for γ ', γ in these alloys.M
23c
6in carbide, be mainly distributed in crystal boundary, crystal boundary is played to strengthening effect.
High-temperature Superheater In A Boiler, high temperature reheater need boi1er tube to become required shape by processes such as bend pipes in manufacturing processed.Bend pipe is divided into clod wash and two kinds of techniques of hot bending.Hot bending is to process more than the recrystallization temperature of material, needs to re-start solution treatment after curved.Clod wash is to process below the recrystallization temperature of material, normally at room temperature processes, and according to the size of deflection, determines whether to re-start solution treatment, avoids solution treatment again in actual production as far as possible.
Ni-based and property heat treatment iron nickel base alloy of solution strengthening type is solution treatment, and its clod wash is carried out after solution treatment.Ni-based and property heat treatment iron nickel base alloy of precipitation strength type is solution treatment+one or many ageing treatment, and its clod wash is carried out after being conventionally arranged in solution treatment, carries out after being also arranged in solid solution+ageing treatment.
After ageing treatment, γ ' in alloy, γ ", carbide separates out in a large number; owing to being distributed in γ ', the γ of intracrystalline, " size is little, quantity is many, and coherence between common and matrix, make room temperature and high-temperature yield strength, the hardness of material significantly increase, and plasticity and toughness significantly reduce.As Inconel740 alloy, room temperature yield strength 300MPa left and right after solution treatment, unit elongation 55% left and right, relative reduction in area reaches 67%, and room temperature impelling strength reaches 250J/cm2, after the ageing treatment of 800 ℃ * 16 hours, more than room temperature yield strength is brought up to 700MPa, unit elongation is reduced to 50%, and relative reduction in area is reduced to 49%, and room temperature impelling strength is reduced to 88J/cm
2.263 alloy solid solutions are processed rear room temperature yield strength 380MPa, unit elongation 64%, room temperature impelling strength 310J/cm
2, after the timeliness of 800 ℃ * 8 hours, room temperature yield strength is brought up to 618MPa, and unit elongation is reduced to 35%, and room temperature impelling strength is reduced to 78J/cm
2.After ageing treatment, the intensity of boi1er tube significantly rises, and the resistance to deformation in bend pipe process is increased, and due to plasticity and toughness attenuating, in bend pipe process, easily cracks.
After solution treatment, directly carry out bend pipe, then carry out ageing treatment or be in operation utilizing service temperature to carry out timeliness, because solid solution state alloy yield strength is low, plasticity and toughness are high, and deformability is strong, have avoided carrying out after timeliness the problems referred to above of bend pipe.Yet test shows, after solution treatment, carry out the distortion such as bend pipe, last ageing treatment or military service process in timeliness, near precipitated phase crystal boundary particularly separating out significantly of carbide reduces, in high temperature long service process subsequently, crystal boundary position does not have enough strengthening phases, first cracking occurs and cause component failure, reduces the life-span.If re-start solid solution or solid solution+ageing treatment after deformation processing, can avoid near the minimizing of the precipitated phase of crystal boundary, but because the temperature of solution treatment is very high, the solution treatment repeating causes grain growth, thermal distortion simultaneously and oxidation are serious, after cooling, need to re-start cold sizing and remove zone of oxidation, cost increases.
Therefore according to existing technique, no matter be after solid solution or after solid solution+timeliness, to carry out the processing such as bend pipe all to have technical problem, have a strong impact on the application in boiler is manufactured of nickel-base alloy and iron nickel base alloy.
Summary of the invention
The object of the present invention is to provide and a kind ofly can solve the clod wash under solid solution condition of nickel-base alloy and iron nickel base alloy boi1er tube and reduce material grain boundary carbide and separate out quantity, thereby reduction creep rupture strength, and under aged, plasticity is low during clod wash, intensity is high, distortion difficulty is the problem of cracking easily, thereby improves the nickel-base alloy of creep rupture strength and the deformation processing technique of iron nickel base alloy of nickel-base alloy and iron nickel base alloy.
For achieving the above object, the technical solution used in the present invention is: by the nickel-base alloy of solution treatment and iron nickel base alloy at the γ ' higher than nickel-base alloy and iron nickel base alloy, the solvent temperature of γ ' ' phase and the Precipitation Temperature of grain boundary carbide, and under solvent temperature lower than carbide, heat-treat, carry out deformation processing after cooling, reach the required profile of parts and size, finally carry out ageing treatment or in hot operation from ageing treatment.
Described nickel-base alloy and iron nickel base alloy are the alloy with the main strengthening phase of γ '.
Described nickel-base alloy and the grain boundary carbide of iron nickel base alloy are M
23c
6type carbide.
Described heat treated temperature is 850 ℃-1050 ℃.
The described cooling Cooling Mode of taking is cooled to separating out below finishing temperature of γ ' phase.
Described Cooling Mode is water-cooled.
The temperature of described deformation processing lower than γ ' or (with) Precipitation Temperature of γ ' ' phase.
The temperature of described deformation processing is room temperature, and deformation processing is clod wash.
Described parts are boi1er tube.
The present invention carries out the thermal treatment of a comparatively high temps to the nickel-base alloy of solution treatment and iron nickel base alloy, in advance carbide precipitate reduce simultaneously or avoid γ ' or (with) γ " separating out of phase; then carry out deformation processing; reach the required profile of parts and size, when finally carrying out ageing treatment (to precipitation strengthening alloy) or utilizing high-temperature service from timeliness solid solution strengthened alloys such as (to 617) 617B.
When of the present invention, what term " thermal treatment of comparatively high temps " defined is that its temperature is at γ ', γ " between the solvent temperature of phase and the solvent temperature of grain boundary carbide than final timeliness thermal treatment (to precipitation strengthening alloy) or a higher intermediate heat treatment of service temperature (to solid solution strengthened alloy) temperature.Due to the difference of different-alloy chemical composition, or the fluctuation of same alloying constituent, its temperature range is different.
When of the present invention, term " deformation processing " definition be the deformation processing below alloy recrystallization temperature.
Compared with prior art, the thermal treatment of the comparatively high temps of the present invention in the middle of increasing once after by solution treatment, its temperature is higher than γ ', γ " solvent temperature of phase and the Precipitation Temperature of grain boundary carbide, and lower than the solvent temperature of carbide, carbide precipitate on crystal boundary, avoid γ ' simultaneously, γ " waits separating out in a large number of matrix precipitate, keep solid solution state alloy yield strength low, the advantage that plasticity and toughness are high, be conducive to the enforcement of bend pipe processing, in ageing treatment subsequently, intracrystalline is separated out γ ', γ " waits strengthening phase, near the strengthening phases such as carbide crystal boundary are retained, thereby guaranteed the performance of parts.The invention solves the clod wash under solid solution condition of nickel-base alloy and iron nickel base alloy boi1er tube and reduce material Carbide Precipitation, thereby reduce creep rupture strength, under aged, plasticity is low during clod wash, intensity is high, and distortion difficulty is the technical problem of cracking easily.
Accompanying drawing explanation
Fig. 1 is deformation processing technique schematic diagram of the present invention;
Fig. 2 is the microtexture of control sample 3 of the present invention;
Fig. 3 is the microtexture of control sample 4 of the present invention;
Fig. 4 is the microtexture of embodiment sample 1;
Fig. 5 is the microtexture of embodiment sample 2;
Fig. 6 is the microtexture of embodiment sample 3;
Fig. 7 is the microtexture after control sample 5 stress ruptures;
Fig. 8 is the microtexture after control sample 6 stress ruptures;
Fig. 9 is the microtexture after embodiment sample 4 stress ruptures.
Embodiment
Below in conjunction with accompanying drawing, the invention will be further described.
Referring to Fig. 1, some non-limiting embodiments disclosed by the invention relates to nickel-base alloy and iron nickel base alloy deformation processing technique, step comprises: by the nickel-base alloy of solution treatment and iron nickel base alloy at the γ ' higher than nickel-base alloy and iron nickel base alloy, γ " solvent temperature of phase and the Precipitation Temperature of grain boundary carbide; and under solvent temperature lower than carbide, heat-treat, carry out deformation processing after cooling; reach the required profile of parts and size, finally carry out ageing treatment or in hot operation from ageing treatment.
Particularly, utilize this technique to carry out bend pipe processing to nickel-base alloy and iron nickel base alloy boi1er tube.
Adopt non-limiting example explanation various nonrestrictive embodiments disclosed by the invention below.
The material of all control sample and embodiment sample is Inconel740H, is a kind of ultra supercritical power generation unit superalloy, and its standard thermal treatment is solid solution (1150 ℃ * 1 hour water-cooled)+timeliness (800 ℃ * 16 hours air coolings).
Embodiment 1
Control sample 1:1150 ℃ * 1 hour solid solution water-cooled, hardness is HB168, R
p0.2for 314MPa.
Control sample 2:1150 ℃ * 1 hour solid solution water-cooled+800 ℃ * 16 hours timeliness air coolings, hardness is brought up to HB304, R
p0.2for 728MPa, intensity and hardness are too high, are not suitable for doing deformation processing.
As with above-mentioned two kinds of existing techniques in the contrast of as-heat-treated condition before deformation processing, material has been carried out respectively to the heat treatment test of differing temps.
Control sample 3:1150 ℃ * 1 hour solid solution water-cooled+700 ℃ * 4 hours thermal treatment air coolings.After thermal treatment, the hardness of control sample 3 is HB268, and Fig. 2 is shown in by microtexture photo, and because temperature is too low, crystal boundary does not have carbide precipitate.
Control sample 4:1150 ℃ * 1 hour solid solution water-cooled+850 ℃ * 2 hours thermal treatment air coolings.After thermal treatment, the hardness of control sample 4 is HB267, and Fig. 3 is shown in by microtexture photo, has Carbide Precipitation on crystal boundary, but due to the solvent temperature of temperature lower than γ ', separating out of intracrystalline γ ' causes hardness slightly high.
1:1150 ℃ * 1 hour solid solution water-cooled+900 of embodiment sample ℃ * 2 hours thermal treatment air coolings; After thermal treatment, the hardness of embodiment sample 1 is HB239, and microtexture is shown in Fig. 4, has Carbide Precipitation on crystal boundary, and hardness is also moderate, R
p0.2for 544MPa, be suitable for deformation processing.
2:1150 ℃ * 1 hour solid solution water-cooled+1010 of embodiment sample ℃ * 2 hours thermal treatment air coolings.After thermal treatment, the hardness of embodiment sample 2 is HB181.5, and microtexture is shown in Fig. 5, has Carbide Precipitation on crystal boundary, and hardness is also moderate, R
p0.2for 455MPa, be suitable for deformation processing.
3:1150 ℃ * 1 hour solid solution water-cooled+900 of embodiment sample ℃ * 2 hours thermal treatment water-cooleds.After thermal treatment, the hardness of embodiment sample 3 is HB229.Embodiment sample 3 adopts water-cooled after processing, with respect to embodiment 1, has further suppressed separating out of γ ' in process of cooling, and hardness is lower, and microtexture is shown in Fig. 6.
Embodiment 2:
Inconel740H has been carried out to the creep rupture test under three kinds of conditions.
Control sample 5: be standard thermal treatment material (1150 ℃ * 1 hour solid solution water-cooled+800 ℃ * 16 hours timeliness air coolings), be processed into creep rupture strength sample and carry out stress rupture test under 750 ℃, 292MPa, rupture time is 503 hours.Fig. 7 be stress rupture sample away from the microtexture photo of fracture area, crystal boundary has obvious carbide to exist.
Control sample 6: the common process that adopts existing deformation processing technology, the material of 1150 ℃ * 1 hour solid solution water-cooled is carried out to 11% cold deformation, then carry out the ageing treatment of 800 ℃ * 16h, be processed into creep rupture strength sample and carry out stress rupture test under 750 ℃, 292MPa, rupture time is 380 hours.Fig. 8 be stress rupture sample away from the microtexture photo of fracture area, grain boundary carbide is starkly lower than control sample 1.
Embodiment sample 4: process according to technique disclosed by the invention, the material of 1150 ℃ * 1 hour solid solution water-cooled is first carried out the intermediate heat treatment of 900 ℃ * 2 hours, R
p0.2for 544MPa, then carry out 11% cold deformation, then carry out the ageing treatment of 800 ℃ * 16h, be processed into creep rupture strength sample and carry out stress rupture test under 750 ℃, 292MPa, rupture time is 435 hours.Fig. 9 be stress rupture sample away from the microtexture photo of fracture area, grain boundary carbide is obviously than control sample more than 2, approaches with control sample 1.
Embodiment 3:
According to technique disclosed by the invention, carry out processing and implementation example sample 5, the material of 1150 ℃ * 1 hour solid solution water-cooled is first carried out the intermediate heat treatment of 1010 ℃ * 2 hours, R
p0.2for 455MPa, then carry out 13% cold deformation, then carry out the ageing treatment of 790 ℃ * 8h, be processed into creep rupture strength sample and carry out stress rupture test under 750 ℃, 292MPa, rupture time is 582.6 hours.Even if deflection is greater than control sample 6, its life-span is still long than control sample 6, even higher than the control sample 5 that there is no deformation processing.
Claims (9)
1. the deformation processing technique of a nickel-base alloy and iron nickel base alloy, it is characterized in that: by the nickel-base alloy of solution treatment and iron nickel base alloy at the γ ' higher than nickel-base alloy and iron nickel base alloy, the solvent temperature of γ ' ' phase and the Precipitation Temperature of grain boundary carbide, and under solvent temperature lower than carbide, heat-treat, carry out deformation processing after cooling, reach the required profile of parts and size, finally carry out ageing treatment or in hot operation from ageing treatment.
2. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: described nickel-base alloy and iron nickel base alloy are the alloy with the main strengthening phase of γ '.
3. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: described nickel-base alloy and the grain boundary carbide of iron nickel base alloy are M
23c
6type carbide.
4. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: described heat treated temperature is 850 ℃-1050 ℃.
5. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: the described cooling Cooling Mode of taking is cooled to separating out below finishing temperature of γ ' phase.
6. nickel-base alloy according to claim 5 and iron nickel base alloy deformation processing technique, is characterized in that: described Cooling Mode is water-cooled.
7. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: the temperature of described deformation processing lower than γ ' or (with) Precipitation Temperature of γ ' ' phase.
8. according to the nickel-base alloy described in claim 1 or 7 and iron nickel base alloy deformation processing technique, it is characterized in that: the temperature of described deformation processing is room temperature, deformation processing is clod wash.
9. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, is characterized in that: described parts are boi1er tube.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018003107A (en) * | 2016-07-04 | 2018-01-11 | 大同特殊鋼株式会社 | PRODUCTION METHOD OF PRECIPITATE TYPE HEAT-RESISTANT Ni-BASED ALLOY |
| CN108588814A (en) * | 2018-06-05 | 2018-09-28 | 西北工业大学 | The preparation method of Ni-based 028 single crystal alloy of iron under solid-state |
| CN113025848A (en) * | 2021-05-24 | 2021-06-25 | 北京钢研高纳科技股份有限公司 | Iron-nickel-based precipitation strengthening type high-temperature alloy and preparation method and application thereof |
| CN113684353A (en) * | 2021-10-27 | 2021-11-23 | 江苏省沙钢钢铁研究院有限公司 | GH2132 alloy and preparation method thereof |
| CN114085965A (en) * | 2021-11-19 | 2022-02-25 | 华能国际电力股份有限公司 | Two-stage solution treatment process for aging-strengthened high-temperature alloy |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0361524B1 (en) * | 1988-09-30 | 1994-05-04 | Hitachi Metals, Ltd. | Ni-base superalloy and method for producing the same |
| EP1146133A1 (en) * | 2000-04-11 | 2001-10-17 | Hitachi Metals, Ltd. | Manufacturing process of nickel-based alloy having improved hot sulfidation-corrosion resistance |
| JP2002088455A (en) * | 2000-09-13 | 2002-03-27 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING Ni-BASE ALLOY HAVING EXCELLENT HIGH TEMPERATURE SULFIDATION CORROSION RESISTANCE |
-
2013
- 2013-12-28 CN CN201310744032.8A patent/CN103710656B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0361524B1 (en) * | 1988-09-30 | 1994-05-04 | Hitachi Metals, Ltd. | Ni-base superalloy and method for producing the same |
| EP1146133A1 (en) * | 2000-04-11 | 2001-10-17 | Hitachi Metals, Ltd. | Manufacturing process of nickel-based alloy having improved hot sulfidation-corrosion resistance |
| JP2002088455A (en) * | 2000-09-13 | 2002-03-27 | Hitachi Metals Ltd | METHOD FOR MANUFACTURING Ni-BASE ALLOY HAVING EXCELLENT HIGH TEMPERATURE SULFIDATION CORROSION RESISTANCE |
| US6562157B2 (en) * | 2000-09-13 | 2003-05-13 | Hitachi Metals, Ltd. | Manufacturing process of nickel-based alloy having improved high temperature sulfidation-corrosion resistance |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018003107A (en) * | 2016-07-04 | 2018-01-11 | 大同特殊鋼株式会社 | PRODUCTION METHOD OF PRECIPITATE TYPE HEAT-RESISTANT Ni-BASED ALLOY |
| CN108588814A (en) * | 2018-06-05 | 2018-09-28 | 西北工业大学 | The preparation method of Ni-based 028 single crystal alloy of iron under solid-state |
| CN113025848A (en) * | 2021-05-24 | 2021-06-25 | 北京钢研高纳科技股份有限公司 | Iron-nickel-based precipitation strengthening type high-temperature alloy and preparation method and application thereof |
| CN113684353A (en) * | 2021-10-27 | 2021-11-23 | 江苏省沙钢钢铁研究院有限公司 | GH2132 alloy and preparation method thereof |
| CN114085965A (en) * | 2021-11-19 | 2022-02-25 | 华能国际电力股份有限公司 | Two-stage solution treatment process for aging-strengthened high-temperature alloy |
| CN114085965B (en) * | 2021-11-19 | 2023-03-10 | 华能国际电力股份有限公司 | Two-stage solution treatment process for aging-strengthened high-temperature alloy |
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