CN103993145A - Method for improving special structure grain-boundary proportion of austenitic stainless steel - Google Patents
Method for improving special structure grain-boundary proportion of austenitic stainless steel Download PDFInfo
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- CN103993145A CN103993145A CN201410189167.7A CN201410189167A CN103993145A CN 103993145 A CN103993145 A CN 103993145A CN 201410189167 A CN201410189167 A CN 201410189167A CN 103993145 A CN103993145 A CN 103993145A
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Abstract
The invention relates to a technological method for improving sigmaCSL (coincidence site lattice) grain-boundary proportion of 316, 304 and other austenitic stainless steel. The method includes: subjecting austenitic stainless steel to solid solution heat treatment at 1000DEG C-1200DEG C; conducting 3%-20% deformation at 300DEG C-900DEG C; and carrying out recrystallization annealing, then performing heat preservation for 5min-1h at 1000DEG C-1200DEG C, thus obtaining the austenitic stainless steel containing a high proportion low sigmaCSL grain boundary. The process has no need to change the material composition and add additional production equipment, is simple and easy to realize, and has very obvious economic benefits.
Description
Technical field
(CSL is the abbreviation of " coincidence site lattice ", and the meaning is coincidence site lattice to the present invention relates to the low Σ CSL of the austenitic stainless steel crystal boundaries such as a kind of raising 316,304.Low Σ CSL refers to Σ≤29) processing method of ratio, belong to deformation and the thermal treatment process technology field of metallic substance.
Background technology
316, the austenitic stainless steels such as 304 have stronger corrosion resistance nature, therefore in industry, have a very wide range of applications.How improving the ability of the intergranular corrosion resistance of austenitic stainless steel, is further to extend its work-ing life, the major issue of increasing economic efficiency.The intergranular corrosion behavior of material and grain boundary structure and character are closely related, therefore can improve the intergranular corrosion resistance performance of austenitic stainless steel by controlling interior special construction crystal boundary (the low Σ CSL crystal boundary) ratio of material and distributing.
Watanabe in 1984 propose the concept of " grain boundary design and control " first.Nineteen ninety-five, the first passage experimental evaluations such as Palumbo " grain boundary design and the control " impact on material intergranular corrosion drag, and further its development has been formed to " crystal boundary engineering " research field.Lin and Palumbo etc. process and can make low Σ CSL crystal boundary bring up to 71% by 37% 600 alloys, and this makes material when the experiment of boiling ferric sulfate immersion corrosion, and erosion rate reduces 30-60%.The Canada company that has this technical patent has registered trade mark " GBE by crystal boundary engineering
tM".Lehockey and Palumbo etc. carry out the lead alloy plate of lead-acid cell after the processing of crystal boundary engineering; low Σ CSL crystal boundary ratio is brought up to more than 70%; corrosion resistance nature obviously improves, and battery charging and discharging cycle index improves 1-3 doubly, and this technology has also obtained the protection of patent.Crystal boundary engineering is to adopt processing deformation and thermal treatment process to produce a large amount of low Σ CSL crystal boundaries, thereby controls structure and the distribution thereof that forms crystal boundary, finally improves a kind of processing method of material corrosion resistance.The main thermomechanical treatment technique of having reported at present has following three kinds of routes: (1) by 3% ~ 8% distortion after, long-time (10 ~ 100h) annealing under a little less than material recrystallization temperature; (2) by after 5% ~ 40% distortion, short period of time (3 ~ 60min) annealing under higher than material recrystallization temperature, and repeat such technique repeatedly; (3) by after 5% ~ 10% distortion, higher than the short period of time under recrystallization temperature (5 ~ 10min), annealing.These processing methodes, by adjusting cold deformation and heat treating regime, can realize the low Σ CSL crystal boundary ratio that increases substantially, and improve the object with crystal boundary correlated performance.Michiuchi etc. impose 3% prestrain to 316 stainless steels, then, at 967 ℃ of annealing 72h, low Σ CSL crystal boundary ratio is brought up to more than 80%.Wang etc. to Pb – Ca – Sn – Al alloy impose 30% cold roller and deformed, then, at 270 ℃ of annealing 10min, this process is repeated to make for 3 times low Σ CSL crystal boundary ratio bring up to 80%.Xia etc. impose 5% cold deformation to 690 alloy pipes, then, at 1100 ℃ of annealing 5min, can make low Σ CSL crystal boundary ratio bring up to more than 70%.
But the processing method of utilizing cold deformation to improve the low Σ CSL of material crystal boundary ratio is often only applicable to sheet material or the tubing of thinner thickness.For the relatively large sheet material of thickness or tubing, after the cold working of small deformation amount, strain often only concentrates on material surface, after final annealing, can not on the whole thickness of material, all low Σ CSL crystal boundary ratio significantly be improved.In addition, in a lot of situations, use hot rolling technology processing austenitic stainless steel, finally carry out again solution treatment.Therefore, the present invention proposes the low Σ CSL crystal boundary ratio that method that another kind utilizes high temperature deformation processing and follow-up recrystallization annealing improves the austenitic stainless steels such as 316,304, in the Face-centred Cubic Metals material of some other low stacking fault energy, also can use with reference to this technique.
Summary of the invention
The processing method that the object of this invention is to provide the low Σ CSL of the austenitic stainless steel crystal boundary ratios such as a kind of raising 316,304.
The object of the invention is to realize by following technique means.
A processing method for the low Σ CSL of the austenitic stainless steel crystal boundary ratios such as raising 316,304, is characterized in that the method has following processing step:
A. by the austenitic stainless steels such as 316,304 1000 ℃ ~ 1200 ℃ solution heat treatment;
B. at 300 ℃ ~ 900 ℃, be out of shape, deflection is 3% ~ 20%;
C. carry out recrystallization annealing, at 1000 ℃ ~ 1200 ℃ insulation 5min ~ 1h, then quench, can obtain the austenitic stainless steels such as 316,304 of the low Σ CSL of higher proportion crystal boundary.Recrystallization process extends soaking time final low Σ CSL crystal boundary ratio is not had much affect.
The present invention, mainly for the austenitic stainless steels such as 316,304, determines high temperature deformation processing and annealing process.After art breading of the present invention, the low Σ CSL crystal boundary ratio in material can reach more than 80% (Palumbo-Aust standard).And in material without art breading of the present invention, low Σ CSL crystal boundary ratio is often lower than 50%.The material material low with low Σ CSL crystal boundary ratio that low Σ CSL crystal boundary ratio is high compared and can obviously be improved material intergranular corrosion resistance and resistance to intergranular stress corrosion performance.
Processing method of the present invention is applied to last procedure in the austenite stainless steel plate materials such as 316,304 or the tubing course of processing, by this technique, can realize and not change alloying constituent and do not adding under the prerequisite of extra production unit and improve the performance that material is relevant to crystal boundary, such as anti intercrystalline corrosion, stress corrosion dehiscence resistant, creep resistance, anti-fatigue performance etc.Material must carry out the high temperature anneal before processing by this technique, guarantees that material does not have deformation.At material, do not have under the state of deformation, carry out at 300 ℃ ~ 900 ℃ 3% ~ 20% machining deformation, deflection will accurately be controlled.After machining deformation, carry out recrystallization annealing, 1000 ℃ ~ 1200 ℃ insulations, quench after 5min ~ 1h, the solid solubility temperature of this temperature and 316, the austenitic stainless steels such as 304 is suitable, can be connected mutually with austenitic stainless steel conventional production process.Recrystallization annealing after this at high temperature little deformation quantity processing can obviously improve the Σ 3 in material
ncrystal boundary (n=1,2,3) ratio, thus the ratio of overall low Σ CSL crystal boundary improved.
Feature of the present invention is: this processing method thermal processing distortion is easily controlled, and does not need to add extra alloying constituent, and need to not increase extra production unit in material produce process.Principal feature is that the austenitic stainless steels such as 316,304 are not being had under the state of deformation, in 300 ℃ ~ 900 ℃ distortion 3% ~ 20%, then carries out high temperature annealing.Technique is simple, easily controls, and has fairly obvious economic benefit.
Accompanying drawing explanation
Fig. 1 is the dissimilar crystal boundary network profile of each sample.Wherein (A) is the sample A crystal boundary network profile that 304 austenitic stainless steels obtain after art breading of the present invention; (B) be that 304 austenitic stainless steels are without the crystal boundary network profile of art breading sample B of the present invention; (C) the sample C crystal boundary network profile obtaining after art breading of the present invention for 316L austenitic stainless steel; (D) 316L austenitic stainless steel is without the crystal boundary network profile of art breading sample D of the present invention.
Embodiment
Below in conjunction with embodiment, the present invention is described in detail:
embodiment mono-
To 304 austenitic stainless steels, (composition quality per-cent is: Cr:18.2%, Ni:8.11%, C:0.019%, Si:0.41%, Mn:1.07%, P:0.038%, S:0.007%, Fe:72.146%) carry out solution treatment, solid solubility temperature is 1100 ℃, insulation 30min, then shrend; At 400 ℃, be rolled thermal distortion 6.5%; Then carry out recrystallization annealing, 1100 ℃ of insulations 20min, then shrends.Obtained A sample is carried out to EBSD(Electron Back-Scattered Diffraction) method mensuration.In order to contrast, to not passing through 304 austenite stainless steel sample B of art breading of the present invention, also carry out EBSD method mensuration.Measurement result is as Fig. 1 (A) with (B).Test result is utilized HKL-Channel 5 data analysis software statistical study, and low Σ CSL crystal boundary is all pressed Palumbo-Aust canonical statistics.Low Σ CSL crystal boundary ratio in A sample is 81.4%, apparently higher than 46.4% low Σ CSL crystal boundary ratio in B sample.
embodiment bis-
316L austenitic stainless steel (mass percent of composition is: 69.98Fe, 16.26Cr, 10.10Ni, 0.028C, 0.47Si, 1.03Mn, 0.044P, 0.005S, 2.08Mo) is carried out to solution treatment, and solid solubility temperature is 1100 ℃, insulation 30min, then shrend; 500 ℃ of stretching thermal distortions 5%; Then at 1100 ℃ of insulation 10min, carry out recrystallization annealing, then shrend, obtains C sample.C sample is carried out to EBSD analytical test.In order to contrast, to not passing through the sample D of art breading of the present invention, carry out equally EBSD test.Measurement result is as Fig. 1 (C) with (D).Test result is utilized HKL-Channel 5 data analysis software statistical study, and low Σ CSL crystal boundary is all pressed Palumbo-Aust canonical statistics.Low Σ CSL crystal boundary ratio in C sample is 82.3%, apparently higher than 57.3% low Σ CSL crystal boundary ratio in D sample.
embodiment tri-
316L austenitic stainless steel (mass percent of composition is: 69.98Fe, 16.26Cr, 10.10Ni, 0.028C, 0.47Si, 1.03Mn, 0.044P, 0.005S, 2.08Mo) is carried out to solution treatment, and solid solubility temperature is 1100 ℃, insulation 30min, then shrend; 300 ℃ of stretching thermal distortions 5%; Then at 1100 ℃ of insulation 10min, carry out recrystallization annealing, then shrend.Obtained sample is carried out to EBSD test, and test result is utilized HKL-Channel 5 data analysis software statistical study, and low Σ CSL crystal boundary is all pressed Palumbo-Aust canonical statistics.Statistical analysis, in sample, low Σ CSL crystal boundary ratio is 80.9%, far away higher than low Σ CSL crystal boundary ratio (57.3%) in the D sample without art breading of the present invention.
embodiment tetra-
316L austenitic stainless steel (mass percent of composition is: 69.98Fe, 16.26Cr, 10.10Ni, 0.028C, 0.47Si, 1.03Mn, 0.044P, 0.005S, 2.08Mo) is carried out to solution treatment, and solid solubility temperature is 1100 ℃, insulation 30min, then shrend; 700 ℃ of stretching thermal distortions 10%; Then at 1100 ℃ of insulation 10min, carry out recrystallization annealing, then shrend.Obtained sample is carried out to EBSD test, and test result is utilized HKL-Channel 5 data analysis software statistical study, and low Σ CSL crystal boundary is all pressed Palumbo-Aust canonical statistics.Statistical analysis, in sample, low Σ CSL crystal boundary ratio is 72.8%, far away higher than low Σ CSL crystal boundary ratio (57.3%) in the D sample without art breading of the present invention.
Claims (1)
1. the method that improves austenitic stainless steel special construction crystal boundary ratio, is characterized in that the method has following processing step:
A. by austenitic stainless steel 1000 ℃ ~ 1200 ℃ solution heat treatment;
B. carry out high temperature deformation, texturing temperature is 300 ℃ ~ 900 ℃, and deflection is 3% ~ 20%;
C. carry out recrystallization annealing, at 1000 ℃ ~ 1200 ℃ insulation 5min ~ 1h, obtain the austenitic stainless steel of the low Σ CSL crystal boundary of higher proportion.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105420472A (en) * | 2015-11-11 | 2016-03-23 | 上海大学 | Grain boundary engineering technique for improving corrosion resistance of 316Lmod stainless steel |
| CN106086582A (en) * | 2016-06-13 | 2016-11-09 | 上海大学兴化特种不锈钢研究院 | The technique improving ferrum Ni-based Incoloy925 alloy low Σ coincidence lattice grain boundary ratio |
| CN107815527A (en) * | 2017-09-29 | 2018-03-20 | 浙江久立特材科技股份有限公司 | Improve the GBE processes of the low ∑ CSL crystal boundary ratios of stainless steel pipe |
| CN108193036A (en) * | 2017-12-18 | 2018-06-22 | 南昌大学 | A kind of method for optimizing the distribution of 316L austenitic stainless steels Grain Boundary Character |
| CN108193024A (en) * | 2017-12-18 | 2018-06-22 | 南昌大学 | A kind of method for improving 316LN austenitic stainless steel special grain boundary ratios |
| CN111020145A (en) * | 2019-10-24 | 2020-04-17 | 南京理工大学 | Preparation method of 304 austenitic stainless steel with high molten salt corrosion resistance |
| CN111235369A (en) * | 2018-11-29 | 2020-06-05 | 南京理工大学 | Method for improving hydrogen embrittlement resistance of 304 austenitic stainless steel |
| CN113373289A (en) * | 2021-04-27 | 2021-09-10 | 常州市联谊特种不锈钢管有限公司 | Thermomechanical treatment method for improving bending property of austenitic stainless steel pipe |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105420472A (en) * | 2015-11-11 | 2016-03-23 | 上海大学 | Grain boundary engineering technique for improving corrosion resistance of 316Lmod stainless steel |
| CN106086582A (en) * | 2016-06-13 | 2016-11-09 | 上海大学兴化特种不锈钢研究院 | The technique improving ferrum Ni-based Incoloy925 alloy low Σ coincidence lattice grain boundary ratio |
| CN106086582B (en) * | 2016-06-13 | 2017-11-07 | 上海大学兴化特种不锈钢研究院 | The technique for improving the low Σ coincidence lattice grain boundaries ratio of the Ni-based Incoloy925 alloys of iron |
| CN107815527A (en) * | 2017-09-29 | 2018-03-20 | 浙江久立特材科技股份有限公司 | Improve the GBE processes of the low ∑ CSL crystal boundary ratios of stainless steel pipe |
| CN108193036A (en) * | 2017-12-18 | 2018-06-22 | 南昌大学 | A kind of method for optimizing the distribution of 316L austenitic stainless steels Grain Boundary Character |
| CN108193024A (en) * | 2017-12-18 | 2018-06-22 | 南昌大学 | A kind of method for improving 316LN austenitic stainless steel special grain boundary ratios |
| CN111235369A (en) * | 2018-11-29 | 2020-06-05 | 南京理工大学 | Method for improving hydrogen embrittlement resistance of 304 austenitic stainless steel |
| CN111020145A (en) * | 2019-10-24 | 2020-04-17 | 南京理工大学 | Preparation method of 304 austenitic stainless steel with high molten salt corrosion resistance |
| CN113373289A (en) * | 2021-04-27 | 2021-09-10 | 常州市联谊特种不锈钢管有限公司 | Thermomechanical treatment method for improving bending property of austenitic stainless steel pipe |
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Application publication date: 20140820 |