CN103710656B - A kind of deformation processing technique of nickel-base alloy and iron nickel base alloy - Google Patents
A kind of deformation processing technique of nickel-base alloy and iron nickel base alloy Download PDFInfo
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Abstract
The invention discloses the deformation processing technique of a kind of nickel-base alloy and iron nickel base alloy, solve grain boundary carbide when nickel-base alloy and iron nickel base alloy deformation processing under solid solution condition reduces material timeliness subsequently or is on active service and precipitate out quantity, thus reducing creep rupture strength, and under aged, during deformation processing, plasticity is low, intensity is high, the technical problem of deformation difficulty easily cracking.It is technically characterized in that the nickel-base alloy to solution treatment and iron nickel base alloy carries out the heat treatment of a higher temperature, near crystal boundary, carbide precipitate reduces simultaneously or avoids the precipitation of intracrystalline γ ' or γ ' ' phase in advance, then deformation processing is carried out, reach the profile needed for parts and size, finally carry out Ageing Treatment and both ensured the processing performance in material deformation processing stage, ensure again the creep rupture strength that product is final.
Description
Technical field
The present invention relates to a kind of alloy deformation processing technique, particularly relate to the deformation processing technique of a kind of nickel-base alloy and iron nickel base alloy.
Background technology
Along with attention to environmental conservation in the world, thermal power industry faces increasing CO2The pressure of the pollution reduction such as greenhouse gases and SOx, NOx, the market competition that thermal power industry is encountered simultaneously is also increasingly sharpening, and this is desirable that power plant reduces cost of electricity-generating further.The effective ways solving these problems are exactly the thermal efficiency improving thermal power generation unit, and the steam parameter improving unit is one of most effective approach improving the thermal efficiency.Current ultra supercritical parameter is developed into from low pressure, middle pressure, high pressure, supertension, subcritical, supercritical successively in historical thermal power plant, and current 600 DEG C of grade ultra supercritical power generation technology in Chinas are substantially ripe at home and abroad.
In order to pursue higher generating efficiency, there has been proposed the research and development plan that vapor (steam) temperature is further increased to 700 DEG C and above advanced ultra supercritical power generation technology in China.Owing to vapor (steam) temperature increases substantially, parts to some high temperature section of unit, such as High-temperature Superheater In A Boiler, high temperature reheater, header and pipeline etc., traditional iron-based heat resisting steel intensity and corrosion resistance etc. can not meet requirement, it is necessary to creep rupture strength is higher, corrosion resistance is better Ni-based or Fe Ni matrix high temperature alloy in employing.
Ni-based and iron nickel base alloy solid solution is divided into solution strengthening type alloy and the big class of precipitation strength type alloy two by schedule of reinforcement.Solution strengthening type alloy is the alloy with solution strengthening for main strengthening mechanism, the distortion of parent metal dot matrix is caused by adding the element (chromium, tungsten, molybdenum etc.) different from parent metal atomic size, addition can reduce the element (such as cobalt) of alloy substrate stacking fault energy and add the element (tungsten, molybdenum etc.) that can slow down matrix element diffusion rate, to strengthen matrix.
Precipitation strength or to claim ageing strengthening alloy be the alloy with precipitation-hardening for main strengthening mechanism, namely by solid solution and Ageing Treatment, precipitates out second-phase (γ ', γ ", carbide etc.), with reinforced alloys from supersaturated solid solution.
Ni-based or iron nickel base alloy for advanced ultra supercritical unit, due to the requirement to parts high temperature long service, main candidate material is based on precipitation strengthening alloy, such as 263 alloys, 625 alloys, Inconel740H and Inconel740 alloy, Haynes282 alloy etc..Even if the part adopted classifies as the alloy of solution strengthening type, such as 617 alloys, 617B(617mod.) alloy, at heat treatment or under arms process also carbide precipitate and γ ' can wait precipitated phase." being mainly distributed on intra-die, owing to its granule is little, quantity is many, and matrix plays important invigoration effect for γ ', γ in these alloys.M23C6It is mainly distributed on crystal boundary Deng carbide, crystal boundary is played invigoration effect.
High-temperature Superheater In A Boiler, high temperature reheater need the shape needed for being become by processes such as bend pipes by boiler tube in the fabrication process.Bend pipe is divided into clod wash and two kinds of techniques of hot bending.Hot bending is the recrystallization temperature processing carried out above at material, needs to re-start solution treatment after curved.Clod wash is to be carried out below processing in the recrystallization temperature of material, it is common that is at room temperature processed, determines the need for re-starting solution treatment according to the size of deflection, avoids solution treatment again in actual production as far as possible.
Ni-based and iron nickel base alloy the property heat treatment of solution strengthening type is solution treatment, and its clod wash carries out after solution treatment.Ni-based and iron nickel base alloy the property heat treatment of precipitation strength type is solution treatment+one or many Ageing Treatment, and its clod wash carries out after being typically arranged at solution treatment, carries out after being also arranged in solid solution+Ageing Treatment.
After Wetted constructures, size is little, quantity is many for γ ' in alloy, γ ", carbide precipitate out in a large number, owing to being distributed in the γ ' of intracrystalline, γ ", and coherence generally and between matrix, the room temperature and high-temperature yield strength, the hardness that make material significantly rise, and plasticity and toughness are greatly lowered.Such as Inconel740 alloy, room-temperature yield strength about 300MPa after solution treatment, elongation percentage about 55%, the contraction percentage of area reaches 67%, and room temperature impact toughness reaches 250J/cm2, after the Ageing Treatment of 800 DEG C × 16 hours, room-temperature yield strength brings up to more than 700MPa, elongation percentage is reduced to 50%, and the contraction percentage of area is reduced to 49%, and room temperature impact toughness is reduced to 88J/cm2.Room-temperature yield strength 380MPa after 263 alloy solid solutions process, elongation percentage 64%, room temperature impact toughness 310J/cm2, after the timeliness of 800 DEG C × 8 hours, room-temperature yield strength brings up to 618MPa, and elongation percentage is reduced to 35%, and room temperature impact toughness is reduced to 78J/cm2.After Ageing Treatment, the intensity of boiler tube significantly rises so that the resistance of deformation in bend pipe process increases, and owing to plasticity and toughness lower, easily cracks in bend pipe process.
Be made directly bend pipe after solution treatment, then carry out Ageing Treatment or be in operation and utilize service temperature to carry out timeliness, owing to solid solution state alloy yield strength is low, plasticity and toughness are high, and deformability is strong, it is to avoid carry out the problems referred to above of bend pipe after timeliness.But test shows, the deformation such as bend pipe are carried out after solution treatment, in last Ageing Treatment or military service process in timeliness, the precipitation of the particularly carbide of the precipitated phase near crystal boundary is greatly reduced, in high temperature long service process subsequently, grain boundary sites does not have enough hardening constituents, first occurs cracking to cause component failure, reduces the life-span.If re-starting solid solution or solid solution+Ageing Treatment after deformation processing, the minimizing of precipitated phase near crystal boundary can be avoided, but owing to the temperature of solution treatment is significantly high, the solution treatment repeated causes grain growth, thermal deformation simultaneously and oxidation are serious, needing after cooling re-start cold sizing and remove oxide layer, cost increases.
Therefore according to existing technique, no matter it is carry out the processing such as bend pipe after solid solution or after solid solution+timeliness all to there is technical problem, has a strong impact on the application in boiler manfacturing of nickel-base alloy and iron nickel base alloy.
Summary of the invention
It is an object of the invention to provide one and can solve the problem that the clod wash under solid solution condition of nickel-base alloy and iron nickel base alloy boiler tube reduces grain boundaries Carbide Precipitation quantity, thus reducing creep rupture strength, and under aged, during clod wash, plasticity is low, intensity is high, the problem of deformation difficulty easily cracking, thus improving the nickel-base alloy of the creep rupture strength of nickel-base alloy and iron nickel base alloy and the deformation processing technique of iron nickel base alloy.
For reaching above-mentioned purpose, the technical solution used in the present invention is: by the nickel-base alloy of solution treatment and iron nickel base alloy at the Precipitation Temperature higher than the solution temperature of nickel-base alloy and the γ ' of iron nickel base alloy, γ ' ' phase and grain boundary carbide, and lower than carrying out deformation processing after carrying out heat treatment, cooling under the solution temperature of carbide, reach the profile needed for parts and size, finally carry out Ageing Treatment or from Ageing Treatment in hot operation.
Described nickel-base alloy and iron nickel base alloy are with the alloy of the main hardening constituent of γ '.
Described nickel-base alloy and the grain boundary carbide of iron nickel base alloy are M23C6Type carbide.
Described heat treated temperature is 850 DEG C-1050 DEG C.
Described cooling takes Cooling Mode to be cooled to below the precipitation 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 boiler tube.
The nickel-base alloy of solution treatment and iron nickel base alloy are carried out the heat treatment of a higher temperature by the present invention, leading carbide precipitate reduce simultaneously or avoid γ ' or (with) " precipitation of phase; then carry out deformation processing; reach the profile needed for parts and size, from timeliness solid solution strengthened alloys such as (to 617) 617B when finally carrying out Ageing Treatment (to precipitation strengthening alloy) or utilize high-temperature service for γ.
As used in this application, what define is an intermediate heat-treatment higher than final aging strengthening model (to precipitation strengthening alloy) or service temperature (to solid solution strengthened alloy) temperature to term " heat treatment of higher temperature ", and its temperature is at γ ', γ " between solution temperature and the solution temperature of grain boundary carbide of phase.Due to the difference of different-alloy chemical composition, or the fluctuation of same alloying component, its temperature range is different.
As used in this application, what term " deformation processing " defined is the deformation processing of below alloy recrystallization temperature.
Compared with prior art, the present invention is by increasing the heat treatment of the higher temperature in the middle of once after solution treatment, its temperature is higher than γ ', γ " solution temperature of phase and the Precipitation Temperature of grain boundary carbide, and lower than the solution temperature of carbide, carbide precipitate on crystal boundary, avoid γ ' simultaneously, γ " waits a large amount of precipitations of matrix precipitate, keep solid solution state alloy yield strength low, plasticity and the high advantage of toughness, be conducive to the enforcement that bend pipe is processed, in Ageing Treatment subsequently, intracrystalline precipitates out γ ', γ " waits hardening constituent, the hardening constituents such as the carbide near crystal boundary are retained, thus ensure that the performance of parts.The invention solves the clod wash under solid solution condition of nickel-base alloy and iron nickel base alloy boiler tube and reduce material Carbide Precipitation, thus reducing creep rupture strength, under aged, during clod wash, plasticity is low, intensity is high, the technical problem of deformation difficulty easily cracking.
Accompanying drawing explanation
Fig. 1 is deformation processing technique schematic diagram of the present invention；
Fig. 2 is the microstructure of control sample 3 of the present invention；
Fig. 3 is the microstructure of control sample 4 of the present invention；
Fig. 4 is the microstructure of embodiment sample 1；
Fig. 5 is the microstructure of embodiment sample 2；
Fig. 6 is the microstructure of embodiment sample 3；
Fig. 7 is the microstructure after control sample 5 stress rupture；
Fig. 8 is the microstructure after control sample 6 stress rupture；
Fig. 9 is the microstructure after embodiment sample 4 stress rupture.
Detailed description of the invention
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 includes: by the nickel-base alloy of solution treatment and iron nickel base alloy higher than the γ ' of nickel-base alloy and iron nickel base alloy, γ " solution temperature of phase and the Precipitation Temperature of grain boundary carbide; and lower than carrying out deformation processing after carrying out heat treatment, cooling under the solution temperature of carbide; reach the profile needed for parts and size, finally carry out Ageing Treatment or from Ageing Treatment in hot operation.
Specifically, utilize this technique that nickel-base alloy and iron nickel base alloy boiler tube are carried out bend pipe processing.
Adopt non-limiting example that various non-limiting embodiments disclosed by the invention are described below.
The material of all control sample and embodiment sample is Inconel740H, and for a kind of ultra supercritical unit high temperature alloy, its standard heat treatment is solid solution (1150 DEG C × 1 hour water-cooled)+timeliness (800 DEG C × 16 hours air coolings).
Embodiment 1
Control sample 1:1150 DEG C × 1 hour solid solution water-cooled, hardness is HB168, Rp0.2For 314MPa.
+ 800 DEG C × 16 hours timeliness air coolings of control sample 2:1150 DEG C × 1 hour solid solution water-cooled, hardness brings up to HB304, Rp0.2Too high for 728MPa, intensity and hardness, be not suitable for doing deformation processing.
As with deformation processing in the existing technique of above two before the contrast of condition of heat treatment, material has been carried out respectively the heat treatment test of different temperatures.
+ 700 DEG C × 4 hours heat treatment air coolings of control sample 3:1150 DEG C × 1 hour solid solution water-cooled.After heat treatment, the hardness of control sample 3 is HB268, and Fig. 2 is shown in by microstructure photo, and owing to temperature is too low, crystal boundary does not have carbide precipitate.
+ 850 DEG C × 2 hours heat treatment air coolings of control sample 4:1150 DEG C × 1 hour solid solution water-cooled.After heat treatment, the hardness of control sample 4 is HB267, and Fig. 3 is shown in by microstructure photo, and crystal boundary has Carbide Precipitation, but due to the temperature solution temperature lower than γ ', the precipitation of intracrystalline γ ' causes that hardness is slightly higher.
+ 900 DEG C × 2 hours heat treatment air coolings of 1:1150 DEG C of embodiment sample × 1 hour solid solution water-cooled；After heat treatment, the hardness of embodiment sample 1 is HB239, and microstructure is shown in Fig. 4, and crystal boundary has Carbide Precipitation, and hardness is also moderate, Rp0.2For 544MPa, it is suitable for deformation processing.
+ 1010 DEG C × 2 hours heat treatment air coolings of 2:1150 DEG C of embodiment sample × 1 hour solid solution water-cooled.After heat treatment, the hardness of embodiment sample 2 is HB181.5, and microstructure is shown in Fig. 5, and crystal boundary has Carbide Precipitation, and hardness is also moderate, Rp0.2For 455MPa, it is suitable for deformation processing.
+ 900 DEG C × 2 hours heat treatment water-cooleds of 3:1150 DEG C of embodiment sample × 1 hour solid solution water-cooled.After heat treatment, the hardness of embodiment sample 3 is HB229.Embodiment sample 3 adopts water-cooled after treatment, relative to embodiment 1, further suppress the precipitation of γ ' in cooling procedure, and hardness is lower, and microstructure is shown in Fig. 6.
Embodiment 2:
Inconel740H has been carried out the creep rupture test under three kinds of conditions.
Control sample 5: for standard heat treatment material (+800 DEG C × 16 hours timeliness air coolings of 1150 DEG C × 1 hour solid solution water-cooled), be processed into creep rupture strength sample 750 DEG C, carry out stress rupture test under 292MPa, rupture time is 503 hours.Fig. 7 is the stress rupture sample microstructure photo away from fracture area, and crystal boundary has obvious carbide to exist.
Control sample 6: adopt the common process of existing deformation processing technology, namely the material of 1150 DEG C × 1 hour solid solution water-cooled is carried out the cold deformation of 11%, then the Ageing Treatment of 800 DEG C × 16h is carried out, be processed into creep rupture strength sample 750 DEG C, carry out stress rupture test under 292MPa, rupture time is 380 hours.Fig. 8 is the stress rupture sample microstructure photo away from fracture area, and grain boundary carbide is significantly lower than control sample 1.
Embodiment sample 4: be processed according to technique disclosed by the invention, namely first carries out the intermediate heat-treatment of 900 DEG C × 2 hours, R to the material of 1150 DEG C × 1 hour solid solution water-cooledp0.2For 544MPa, then carry out the cold deformation of 11%, then carry out the Ageing Treatment of 800 DEG C × 16h, be processed into creep rupture strength sample 750 DEG C, carry out stress rupture test under 292MPa, rupture time is 435 hours.Fig. 9 is the stress rupture sample microstructure photo away from fracture area, and grain boundary carbide is ratio control sample more than 2 substantially, close with control sample 1.
Embodiment 3:
It is processed embodiment sample 5 according to technique disclosed by the invention, namely the material of 1150 DEG C × 1 hour solid solution water-cooled is first carried out the intermediate heat-treatment of 1010 DEG C × 2 hours, Rp0.2For 455MPa, then carry out the cold deformation of 13%, then carry out the Ageing Treatment of 790 DEG C × 8h, be processed into creep rupture strength sample 750 DEG C, carry out stress rupture test under 292MPa, rupture time is 582.6 hours.Even if deflection is more than control sample 6, its life-span is still long than control sample 6, even above the control sample 5 not having deformation processing.
Claims (7)
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 higher than the γ ' of nickel-base alloy and iron nickel base alloy, γ " solution temperature of phase and the Precipitation Temperature of grain boundary carbide; and lower than carrying out deformation processing after carrying out intermediate heat-treatment, cooling under the solution temperature of carbide; reach the profile needed for parts and size, finally carry out Ageing Treatment or from Ageing Treatment in hot operation；
Wherein, described nickel-base alloy and iron nickel base alloy are with the γ ' alloy for main hardening constituent；
The temperature of described intermediate heat-treatment is 850 DEG C-1050 DEG C.
2. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, it is characterised in that: described nickel-base alloy and the grain boundary carbide of iron nickel base alloy are M23C6Type carbide.
3. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, it is characterised in that: described cooling takes Cooling Mode to be cooled to below the precipitation finishing temperature of γ ' phase.
4. nickel-base alloy according to claim 3 and iron nickel base alloy deformation processing technique, it is characterised in that: described Cooling Mode is water-cooled.
5. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, it is characterised in that: the temperature of described deformation processing lower than γ ' or/and the γ " Precipitation Temperature of phase.
6. nickel-base alloy and iron nickel base alloy deformation processing technique according to claim 1 or 5, it is characterised in that: the temperature of described deformation processing is room temperature, and deformation processing is clod wash.
7. nickel-base alloy according to claim 1 and iron nickel base alloy deformation processing technique, it is characterised in that: described parts are boiler tube.
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| JP6805583B2 (en) * | 2016-07-04 | 2020-12-23 | 大同特殊鋼株式会社 | Manufacturing method of precipitation 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 |
| CN113025848B (en) * | 2021-05-24 | 2021-08-17 | 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 |
| CN113684353B (en) * | 2021-10-27 | 2022-02-11 | 江苏省沙钢钢铁研究院有限公司 | GH2132 alloy and preparation method thereof |
| 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 |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| 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 |
| US6562157B2 (en) * | 2000-09-13 | 2003-05-13 | Hitachi Metals, Ltd. | Manufacturing process of nickel-based alloy having improved high temperature sulfidation-corrosion resistance |
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Patent 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 |
| US6562157B2 (en) * | 2000-09-13 | 2003-05-13 | Hitachi Metals, Ltd. | Manufacturing process of nickel-based alloy having improved high temperature sulfidation-corrosion resistance |
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