CN100400700C - Process for improving 690 alloy material corrosive-resisting performance - Google Patents
Process for improving 690 alloy material corrosive-resisting performance Download PDFInfo
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- CN100400700C CN100400700C CNB2007100387315A CN200710038731A CN100400700C CN 100400700 C CN100400700 C CN 100400700C CN B2007100387315 A CNB2007100387315 A CN B2007100387315A CN 200710038731 A CN200710038731 A CN 200710038731A CN 100400700 C CN100400700 C CN 100400700C
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Abstract
A method for improving 690 alloy anti-corrosion performance is carried out by keeping temperature at 1100degree for 15mins, water cooling, cold rolling while deforming by 3-10%, re-crystallizing, annealing, keeping temperature at 1050-1150degree for 5-30mins and water cooling. It's simple, convenient and economical.
Description
Technical field
The present invention relates to a kind of processing method of raising 690 alloy material corrosion resistance natures, belong to the deformation and the thermal treatment process technology field of metallic substance.
Background technology
Ni base 690 alloys are face-centered cubic metallic substance of a kind of low stacking fault energy, an its important application aspect is the heat transfer tubing as pressurized water reactor nuclear power station steam generator, improve the intergranular corrosion resistance and the anti-stress corrosion performance of this tubing, be prolongation vapour generator work-ing life, improve a major issue of nuclear power economy.Many performances of material all have confidential relation with the characteristic of crystal boundary, as the transgranular fracture, the burn into diffusion that take place in the material, gather partially, influence that problem such as slippage all is subjected to grain boundary structure.Same crystal boundary characteristic also has a significant impact the corrosion resistance of 690 alloys.
The notion that the eighties the crystal boundary design occurred and controlled in last century, development has formed " crystal boundary engineering " this research field then.The content of this area research mainly comprises: (CSL is the abbreviation of " coincidence site lattice " to the low ∑ CSL crystal boundary ratio of research control and raising, and the meaning is a heavy site battle array.Low ∑ CSL is meant ∑≤29) processing method; Study the relation of some performances relevant and low ∑ CSL crystal boundary ratio and spatial distribution thereof with crystal boundary.Crystal boundary engineering research at present mainly concentrates on the face-centered cubic metallic substance of low stacking fault energy, improve the ratio of low ∑ CSL crystal boundary in this class material based on the formation of annealing twin, that has reported at present mainly contains two kinds of operational paths: (1) by the 3%-8% distortion after, long-time (10-100h) annealing under a little less than the material recrystallization temperature; (2), be higher than recrystallization temperature short period of time (3-60min) annealing, and repeating such technology 3-7 time by after the distortion of 15%-40%.These two kinds of technologies can both obviously improve the low ∑ CSL crystal boundary ratio of material, thereby significantly improve the multiple performance relevant with crystal boundary.After using first kind of technology to make 304 stainless low ∑ CSL crystal boundary ratios bring up to more than 80%, erosion rate reduces more than 75%.After using second kind of art breading to make the low ∑ CSL crystal boundary ratio of Inconel600 alloy bring up to 60-70%, erosion rate can reduce 30-60%.These methods also are applied in lead alloy and brass, but also do not report in 690 alloys.The advantage of these processing methodes is to change material composition, only needs to adjust cold rolling and heat treating regime, just can significantly improve low ∑ CSL crystal boundary ratio in the material, improves the multiple performance relevant with crystal boundary.But first kind of arts demand annealed for a long time, and second kind of arts demand cold working and annealing repeatedly, these two kinds of technologies all are unfavorable for the cost control in the industrial production.Improve low ∑ CSL crystal boundary ratio in 690 alloys so the present invention proposes another kind of processing method, in the face-centered cubic metallic substance of some other low stacking fault energy, also can consult and use.
Summary of the invention
The processing method that the purpose of this invention is to provide a kind of raising 690 alloy material corrosion resistance natures.
The objective of the invention is to realize by following technique means.
A kind of processing method of raising 690 alloy material corrosion resistance natures is characterized in that this method has following processing step:
A. 690 alloy materials are incubated 15min, water-cooleds then at 1100 ℃;
B. carry out cold roller and deformedly, deflection is 3～10%;
C. carry out recrystallization annealing, at 1050～1150 ℃ of insulation 5～30min, water-cooled then, can get high corrosion resistance can 690 alloy materials.
The present invention is primarily aimed at 690 alloys, and (mass percent of composition is: 60.52Ni, 28.91Cr, 9.45Fe, 0.025C, 0.008N, 0.4Ti, 0.34Al, 0.14Si), determine cold rolling and annealing process, obtain low ∑ CSL (heavy site battle array) crystal boundary ratio and be higher than the material of 70% (Palumbo-Aust standard), low ∑ CSL crystal boundary ratio is 46% in the traditional technology material processed.The material that the high material of low ∑ CSL crystal boundary ratio and low ∑ CSL crystal boundary ratio are low is compared and can obviously be improved material intergranular corrosion resistance performance.When being applied to chemical industry to 690 alloys, this is suitable for too.
Processing method of the present invention is last procedure that is applied in 690 alloy pipes, the plate forming course of processing, can be implemented in the intergranular corrosion resistance performance that improves material under the prerequisite that does not change alloying constituent by this technology.To other performance relevant, improvement is also arranged as stress corrosion resistant, creep, fatigue property with crystal particle crystal boundary.Material must carry out high-temperature heat treatment earlier before handling, guaranteeing can not have the deformation energy storage in the material.Material carries out 3～10% cold roller and deformed (variation in thickness with material is calculated) under the state that does not have the deformation energy storage then, and cold rolling reduction will accurately be controlled in such scope.Carry out recrystallization annealing after cold rolling, water-cooled after 1050～1150 ℃ of short period of time insulations, temperature will be higher than solid solubility temperature, like this, can not influence the migration of general big angle crystal boundary in the recrystallization process because of carbide precipitate.Recrystallization annealing behind this little deformation quantity can obviously improve the ∑ 3 in the material
nCrystal boundary (n=1,2,3) ratio, thus overall ratio of hanging down ∑ CSL crystal boundary improved.The soaking time of recrystallization annealing is controlled in 5～30min scope, continues to prolong soaking time low ∑ CSL crystal boundary ratio is obviously reduced.
Characteristics of the present invention are: this processing method neither needs long annealing, does not also need cold deformation repeatedly and annealing (being different from disclosed two kinds of technology parts).Principal feature be to 690 alloy materials under the state that does not have the deformation energy storage, it is cold rolling to carry out the small deformation amount, carries out recrystallization annealing between high temperature, short time then, so technology is simpler, operation easily.Has fairly obvious economic benefit.
Description of drawings
Fig. 1 is the sample A (72% low ∑ CSL crystal boundary) that contains the low ∑ CSL crystal boundary of different ratios, B (70% low ∑ CSL crystal boundary) and C (46% low ∑ CSL crystal boundary), the relation of unit surface corrosion weight loss and etching time.
Fig. 2 is the sample (a) that contains 72% low ∑ CSL crystal boundary, contains the sample (b) of 70% low ∑ CSL crystal boundary and contains the sample (c) of 46% low ∑ CSL crystal boundary, the surface topography after corroding through 216 hours.
Embodiment
After now embodiments of the invention specifically being described in.
Embodiment 1
With 690 alloys (mass percent of composition is: 60.52Ni, 28.91Cr, 9.45Fe, 0.025C, 0.008N, 0.4Ti, 0.34Al, 0.14Si) sheet material 1100 ℃ the insulation 15min, water-cooleds then; After cold rolling 5%, carry out recrystallization annealing, be incubated 5min (A sample) and insulation 30min (B sample), water-cooled then respectively at 1100 ℃.Measure through EBSD (Electron Back-Scattered Diffraction) method, the low ∑ CSL crystal boundary ratio in the A sample is 72%, and the low ∑ CSL crystal boundary ratio in the B sample is 70%.In order to contrast, adopt the sample after traditional technology is handled to measure through the EBSD method, low ∑ CSL crystal boundary ratio is 46% (C sample).Low ∑ CSL crystal boundary is all pressed the Palumbo-Aust canonical statistics.At 715 ℃ of insulation 2h, air cooling is handled as the sensitization that is used for Huey test then with these three kinds of samples.With the method for electropolishing with the sample surfaces cleaning clean after, surface measurements area, and to samples weighing.Be immersed in the solution then and corrode, the composition of solution is: 65%HNO
3+ 0.4%HF, experiment is carried out in room temperature.Sample was taken out water in per 24 hours and clean 3 times, be immersed in the alcohol 10 minutes then, take out the back and dries with hair dryer.Weigh then, obtain corrosion weight loss.Such corrosion test has been carried out 216 hours altogether.Sample surfaces scanning electron microscopic observation after the corrosion.
Fig. 1 contains the corrosion weight loss of low ∑ CSL crystal boundary 690 alloy samples of different ratios and the relation of etching time.As can be seen from Figure, low ∑ CSL crystal boundary ratio is that 46% C sample corrosion weight loss is obviously serious than hanging down the B sample that ∑ CSL crystal boundary ratio is respectively 72% A sample and 70%.The principal feature of intergranular corrosion weightlessness is that the crystal grain of material surface comes off after corrosion.Through 216 hours corrosion, sample A and B surface had only seldom that part crystal grain comes off, and the crystal grain on sample C surface almost comes off fully, as shown in Figure 2.The ratio of the low ∑ CSL crystal boundary of this explanation has very big influence to the intergranular corrosion performance, and the sample that low ∑ CSL crystal boundary ratio is high is obvious than the low sample intergranular corrosion resistance of low ∑ CSL crystal boundary ratio.
Claims (1)
1. processing method that improves 690 alloy material corrosion resistance natures is characterized in that this method has following processing step:
A. 690 alloy materials are incubated 15min, water-cooleds then at 1100 ℃;
B. carry out cold roller and deformedly, deflection is 3～10%;
C. carry out recrystallization annealing, at 1050～1150 ℃ of insulation 5～30min, water-cooled then, can get high corrosion resistance can 690 alloy materials.
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| CNB2007100387315A CN100400700C (en) | 2007-03-29 | 2007-03-29 | Process for improving 690 alloy material corrosive-resisting performance |
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| CNB2007100387315A CN100400700C (en) | 2007-03-29 | 2007-03-29 | Process for improving 690 alloy material corrosive-resisting performance |
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| CN100400700C true CN100400700C (en) | 2008-07-09 |
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Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
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| DE102008047329B3 (en) * | 2008-09-16 | 2009-07-23 | Alstom Technology Ltd. | Producing and mounting nickel alloy-based superheater tube coils, for steam generators, includes forming and hardening tubes in workshop before mounting and hardening weld seams on site |
| DE102008047330B3 (en) | 2008-09-16 | 2009-07-23 | Alstom Technology Ltd. | Process for the factory prefabrication of a heat-treated steel nickel alloy serpentine pipe in sections and subsequent on-site assembly |
| CN102952933B (en) * | 2012-11-20 | 2014-11-05 | 浙江久立特材科技股份有限公司 | Process for improving Incoloy 800 alloy pipe corrosion resistance |
| CN103484803A (en) * | 2013-10-12 | 2014-01-01 | 钢铁研究总院 | Processing technique of nickel-based heat-resisting alloy boiler pipe |
| CN105886841A (en) * | 2016-06-13 | 2016-08-24 | 上海大学兴化特种不锈钢研究院 | Technology for increasing proportion of low sigma coincidence site lattice grain boundary of nickel-base superalloy Hastelloy N |
| CN108754386A (en) * | 2018-07-27 | 2018-11-06 | 北方工业大学 | Thermal shock resistant MCrAlY coating and preparation method thereof |
| CN111020428A (en) * | 2020-01-14 | 2020-04-17 | 上海大学 | Grain boundary engineering process method for adjusting η phase distribution in nickel-based superalloy |
| CN113667913B (en) * | 2021-06-11 | 2022-07-08 | 上海大学 | Process method for improving Hastelloy N alloy Sigma CSL crystal boundary proportion |
| CN115852283B (en) * | 2023-03-08 | 2023-05-02 | 太原科技大学 | High-strength plastic nickel-based alloy plate with double-peak structure and preparation method thereof |
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| CN1354804A (en) * | 1999-04-03 | 2002-06-19 | 德累斯顿固体材料研究所 | Nickel-based metallic material and method for producing same |
| CN1549751A (en) * | 2001-08-30 | 2004-11-24 | ����˹��Э��������Ĺ�������о��� | Method for producing metallic strips |
| DE102005013368B3 (en) * | 2005-03-16 | 2006-04-13 | Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. | Making nickel-based blank with cubic recrystallization structure for use as backing for high temperature superconductor, employs silver micro-alloying and specified thermal and mechanical treatments |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1354804A (en) * | 1999-04-03 | 2002-06-19 | 德累斯顿固体材料研究所 | Nickel-based metallic material and method for producing same |
| CN1549751A (en) * | 2001-08-30 | 2004-11-24 | ����˹��Э��������Ĺ�������о��� | Method for producing metallic strips |
| DE102005013368B3 (en) * | 2005-03-16 | 2006-04-13 | Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. | Making nickel-based blank with cubic recrystallization structure for use as backing for high temperature superconductor, employs silver micro-alloying and specified thermal and mechanical treatments |
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