CN103103327A - Thermal treatment technology of ultrahigh-strength stainless steel - Google Patents
Thermal treatment technology of ultrahigh-strength stainless steel Download PDFInfo
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Abstract
The invention relates to a thermal treatment technology of ultrahigh-strength stainless steel for a long blade of a steam turbine. Based on the original thermal treatment technology of a martensite precipitation hardening stainless steel forging, an intermediate treatment process-cold treatment process is added between a solution treatment process and an aging treatment process, and the method specifically comprises the following steps of: performing solution treatment, and cooling; performing cold treatment at (-5)-2 DEG C for at least one hour; and performing aging treatment. The optimized thermal treatment technology solves the problem of low strength caused by incomplete conversion of austenite to martensite in the original technology, and realizes good matching among strength, plasticity and toughness. The production verification test indicates that by adopting the optimized thermal treatment technology, the performance indexes of the material completely meet the usability requirement of the steel for a long blade of a steam turbine.
Description
Technical field
The present invention relates to the superhigh strength stainless steel field, particularly, the present invention relates to a kind of superhigh strength stainless steel thermal treatment process.
Background technology
Long Turbine Blades, particularly airway length all has higher requirement greater than the Long Turbine Blades of 1.2m to tensile strength, toughness, ductile fracture, high and low all fatigue strength and the performances such as different media corrosion fatigue strength and erosion wear resistance, wherein the coupling of intensity, plasticity and toughness is the leading indicator of conventional examination, and the requirement of these performance requriementss and some component of aviation field matches.So, at present the research tendency of Long Turbine Blades material is to satisfy the performance requriements of Long Turbine Blades through the improvement of series of process from selecting the outstanding material of achievement in the aeronautical material field, has shortened like this design of material cycle and has saved expense.
Usually tensile strength higher than 800MPa, yield strength is called high-strength stainless steel higher than the stainless steel of 500MPa, and yield strength is called superhigh strength stainless steel higher than the stainless steel of 1380MPa.Martensitic precipitation is a kind of of high-strength stainless steel, the intensity of this class steel is processed to realize by martensitic transformation and precipitation hardening, advantage is that intensity is higher, due to low-carbon (LC), Gao Ge, high molybdenum and/or high-copper, its solidity to corrosion generally can be lower than the 18Cr-8Ni austenitic stainless steel simultaneously; Easily cutting, easily welding, postwelding does not generally need spot anneling, and thermal treatment process is also fairly simple.
13Cr-8Ni-2.2Mo-1.1Al steel (chemical composition sees Table 1) is a kind of of martensitic precipitation.It not only has high rigidity and good over-all properties, but and this steel large section through hardening and obtain consistent vertical, horizontal performance.This steel corrosion resisting property is better than 1Cr13 and 0Cr17Ni2 Martensite Stainless Steel, has the anti-general corrosion ability suitable with 17-4PH and good stress corrosion resistant ability, is suitable as the manufacturing Long Turbine Blades.
Table 1 chemical composition (wt%)
13Cr-8Ni-2.2Mo-1.1Al steel does not explicitly call for as On Impact Toughness in the performance requriements of aviation forging, and the Long Turbine Blades On Impact Toughness explicitly calls for, and desired strength and toughness reach matched well.One of ordinary skill in the art have begun to improve stainless toughness and intensity by improving the thermal treatment process of high-strength stainless steel at present, but the high-strength stainless steel performance that obtains all can not reach requirement.
For example CN 101509056A provides the heat treating method of a kind of martensitic precipitation FV520B, specifically martensitic precipitation FV520B is carried out the short period of time tempering at comparatively high temps, take afterwards the mode of Slow cooling, make this martensitic precipitation have good toughness and intensity combination.But the method is only applicable to martensitic precipitation medium to requirement of strength and that toughness reguirements is higher, but Long Turbine Blades is more prone to obtain higher intensity to the requirement with material, reverse turns austenitic existence and can greatly reduce the intensity of material, so heat treating method is not suitable for the manufacturing Long Turbine Blades.
Therefore, in the urgent need to carrying out series of experiments, original thermal treatment process of 13Cr-8Ni-2.2Mo-1.1Al steel forgings is improved, to satisfy the performance requriements of Long Turbine Blades.
Summary of the invention
For the deficiencies in the prior art, one of purpose of the present invention is to provide a kind of thermal treatment process of martensitic precipitation.The present invention is that solution treatment operation in the conventional thermal treatment process of martensitic precipitation increases ice-cold treatment process in ageing treatment process, to reach the coupling of intensity, plasticity and toughness.Reason is as follows: through solution treatment and the tissue after being cooled to normal temperature be that martensitic matrix includes a small amount of austenite+a small amount of delta ferrite, have austenite structure due under normal temperature, this moment, steel had good cold working property, was easy to be shaped and welding.Carry out subsequently ageing treatment, residual austenite begins to change into martensite, but the velocity of diffusion of atom in delta ferrite is than large several orders of magnitude in austenite, cause delta ferrite too much, and delta ferrite does not participate in martensitic transformation, cause martensitic transformation incomplete, reduced the intensity of steel.Therefore and the Ms of martensitic precipitation and finishing temperature Mf are lower, can not become martensitic stainless steel fully under room temperature, should increase the deepfreeze operation, and then timeliness, the intermediate treatment of carrying out later on as solution treatment.The production proof test shows, after adopting the thermal treatment process of optimizing, the property indices of material satisfies Long Turbine Blades fully with the use properties requirement of steel.
Described thermal treatment process comprises the following steps:
(1) solution treatment, cooling;
(2) ice-cold processing: temperature-5 ~ 2 ℃, at least 1 hour;
(3) ageing treatment.
Preferably, described martensitic precipitation is the 13Cr-8Ni-2.2Mo-1.1Al steel.
Preferably, described solid solution temperature is 900 ℃ ~ 1040 ℃, more preferably 910 ~ 950 ℃, and particularly preferably 925 ℃.
Preferably, the described solution treatment time is at least 0.5 hour, such as 0.51 hour, 0.6 hour, 1 hour, 2 hours, 3 hours, 5 hours, 10 hours etc., is particularly preferably at least 1 hour.
Preferably, after described solution treatment, cooling terminal point is below 20 ℃, such as 19 ℃, 17 ℃, 15 ℃, 14 ℃, 12 ℃, 0 ℃, 8 ℃, 6 ℃, 4 ℃, 2 ℃ etc., more preferably below 18 ℃, is particularly preferably below 16 ℃.
Preferably, after described solution treatment, the type of cooling is air-cooled; Speed of cooling is excessively slow, and austenitic transformation is that martensite is incomplete; Speed of cooling is too fast, for example adopts water-cooled, can produce larger quenching stress, easily causes workpiece deformation or cracking; Adopt air-cooledly, easily realize energy-conserving and environment-protective again.
Preferably, described ice-cold treatment temp is-2 ~ 1 ℃, is particularly preferably 0 ~ 1 ℃; Preferably, described ice-cold processing is carried out in frozen water.
The described ice-cold treatment time can be 1.1 hours, 1.2 hours, 1.5 hours, 1.9 hours, 2.1 hours, 2.5 hours, 3 hours, 5 hours, 10 hours etc., is preferably at least 2 hours.
Preferably, cooling after described ice-cold processing; Preferably, after described ice-cold processing, cooling terminal point is room temperature; Preferably, be cooled to air cooling after described ice-cold processing; Cooling after described ice-cold processing refers to the temperature that the temperature that makes steel returns to room temperature or needs.
Preferably, described aging temperature is 520 ~ 570 ℃, more preferably 530 ~ 550 ℃, is particularly preferably 530 ~ 535 ℃; 13Cr-8Ni-2.2Mo-1.1Al martensitic precipitation mainly relies on the tiny lath martensite of high density dislocation and the B2 type ordered phase β of disperse educt-NiAl to strengthen, 530 ℃ of left and right aging strengths reach peak value; Higher than 535 ℃ of timeliness, β-NiAl particle is grown up gradually, lose the coherence relation with matrix gradually, and reverse turns austenitic content constantly to be increased, therefore, aging temp too high (〉=535 ℃) timeliness, intensity obviously descends, low strength can not satisfy Long Turbine Blades to the strength property requirement of Blade Steel.
Preferably, the described ageing treatment time is at least 2 hours, such as 2.1 hours, 2.2 hours, 2.5 hours, 2.9 hours, 3.1 hours, 3.5 hours, 3.9 hours, 4.1 hours, 4.5 hours, 5 hours, 8 hours, 10 hours, 15 hours, 20 hours etc., more preferably at least 3 hours, be particularly preferably at least 4 hours.
Preferably, cooling after described ageing treatment; Preferably, after described ageing treatment, cooling terminal point is room temperature; Preferably, be cooled to air cooling after described ageing treatment.
One of purpose of the present invention also is to provide a kind of martensitic precipitation, and described martensitic precipitation is obtained by above-mentioned thermal treatment process, is a kind of superhigh strength stainless steel.
One of purpose of the present invention also is to provide a kind of purposes of described martensitic precipitation, and described martensitic precipitation can be used as Long Turbine Blades.Preferably, described Long Turbine Blades airway length is greater than 1.2m.
One of purpose of the present invention also is to provide a kind of 13Cr-8Ni-2.2Mo-1.1Al steel.The composition of described 13Cr-8Ni-2.2Mo-1.1Al steel sees Table 1, it is characterized in that, described 13Cr-8Ni-2.2Mo-1.1Al steel is obtained by above-mentioned thermal treatment process, is a kind of superhigh strength stainless steel.
Principle is as follows: through solution treatment and the tissue after being cooled to normal temperature be that martensitic matrix includes a small amount of austenite+a small amount of delta ferrite, have austenite structure due under normal temperature, this moment, steel had good cold working property, was easy to be shaped and welding.Carry out subsequently ageing treatment, residual austenite begins to change into martensite, but the velocity of diffusion of atom in delta ferrite is than large several orders of magnitude in austenite, cause delta ferrite too much, and delta ferrite does not participate in martensitic transformation, cause martensitic transformation incomplete, reduced the intensity of steel.And the Ms of 13Cr-8Ni-2.2Mo-1.1Al steel and finishing temperature Mf are lower, can not become martensitic stainless steel fully under room temperature, should increase the deepfreeze operation, and then timeliness, the intermediate treatment of carrying out later on as solution treatment.
One of purpose of the present invention also is to provide a kind of purposes of described 13Cr-8Ni-2.2Mo-1.1Al steel, and described 13Cr-8Ni-2.2Mo-1.1Al steel can be used as Long Turbine Blades, particularly preferably as the Long Turbine Blades of airway length greater than 1.2m.
Compared with prior art, beneficial effect of the present invention is as follows:
(1) compare original thermal treatment process of precipitation hardening of martensitic stainless steel (particularly 13Cr-8Ni-2.2Mo-1.1Al steel), optimization thermal treatment process of the present invention has increased the intermediate treatment operation, make residual austenite further change martensite into, improved the intensity of material;
(2) compare existing other cryogenic treating process such as cooled with liquid nitrogen, dry ice cooling etc., the ice-cold treatment process safety coefficient that the present invention adopts is high, environmental protection, and low for equipment requirements, simple to operate, be easy to control, greatly reduced production cost.
Description of drawings
Fig. 1 is the mirco structure photo (500 *, 6 grades of grain fineness numbers) at Long Turbine Blades blade root position in the present invention;
Fig. 2 is the mirco structure photo (500 *, 5 ~ 6 grades of grain fineness numbers) of Long Turbine Blades leaf top bit in the present invention.
Embodiment
For ease of understanding the present invention, it is as follows that the present invention enumerates embodiment.Those skilled in the art should understand, described embodiment helps to understand the present invention, should not be considered as concrete restriction of the present invention.
Embodiment 1: carry out 13Cr-8Ni-2.2Mo-1.1Al steel raw material heat treatment process test, grope the feasibility of selected multiple heat-treatment protocol and filter out more excellent thermal treatment process
The thermal treatment concrete technology is as shown in table 2, and the mechanical property result is as shown in table 3.
Table 2 starting material heat treatment test scheme
Table 3 mechanical property detected result
According to the experimental result of table 3, preferred thermal treatment process: solid solution: 925 ℃ ± 15 ℃, 0.5h, be chilled to below 16 ℃ at least, then ice-cold processing: 0 ~ 1 ℃ of frozen water, 2h, take out at least, and air cooling is to room temperature, last timeliness: 530 ℃ ~ 550 ℃, 4h at least, air cooling is to room temperature.
Embodiment 2: intend Long Turbine Blades blade root deflection with the 13Cr-8Ni-2.2Mo-1.1Al punching block and carry out deformation test, further preferred heat treatment process parameter
The concrete technology parameter is as shown in table 4, and mechanical property is shown in Table 5.
Table 4 distortion forging heat treatment test scheme
The mechanical property detected result of table 5 distortion forging
According to the result of table 5, in preferred thermal treatment process, aging temp is 530 ℃ ~ 535 ℃.
Embodiment 3: adopt preferred thermal treatment process that the 1:1 Long Turbine Blades is heat-treated, checking institute is the adaptability of thermal treatment process preferably
Adopt the preferred thermal treatment process of embodiment 1 and embodiment 2 to process the 1:1 Long Turbine Blades of 13Cr-8Ni-2.2Mo-1.1Al steel.Described thermal treatment process is: solid solution: 925 ℃ ± 15 ℃, 1h at least is chilled to below 16 ℃, then ice-cold processing: 0 ~ 1 ℃ of frozen water, and 2h, take out at least, and air cooling is to room temperature, last timeliness: 530 ℃ ~ 535 ℃, 4h at least, air cooling is to room temperature.
Long Turbine Blades blade root and leaf top mechanical property detected result are as shown in table 6.Fig. 1 and Fig. 2 are respectively blade root position and metallographic structure photo corresponding to leaf top bit.
The mechanical property detected result of table 6 Long Turbine Blades
Can be found out by experimental result, the mechanical property of Long Turbine Blades and microstructure all satisfy Long Turbine Blades to the use properties requirement of Blade Steel, have further verified the feasibility of preferred system of heat treatment process.
Embodiment 4
With precipitation hardening of martensitic stainless steel 17-4PH(0Crl7Ni4Cu4Nb) make the 1:1 Long Turbine Blades, heat-treat, comprising: solution treatment: carried out solution treatment 0.5 hour at 1040 ℃, air-cooled to 20 ℃; Ice-cold processing: ice-cold processing is 3 hours in 1 ~ 2 ℃ of frozen water, and air cooling is to room temperature; Ageing treatment: processed 2 hours at 570 ℃, air cooling is to room temperature.
Long Turbine Blades after thermal treatment is tested, and test result is as shown in table 7.
Table 7
Embodiment 5
Precipitation hardening of martensitic stainless steel 13Cr-8Ni-2.2Mo-1.1Al is made the 1:1 Long Turbine Blades, heat-treat, comprising: solution treatment: carried out solution treatment 1 hour at 900 ℃, air-cooled to 20 ℃; Ice-cold processing: ice-cold processing is 1 hour in-5 ~ 0 ℃ of frozen water, and air cooling is to room temperature; Ageing treatment: processed 8 hours at 520 ℃, air cooling is to room temperature.
Long Turbine Blades after thermal treatment is tested, and test result is as shown in table 8.
Table 8
By above experimental result as can be known, the present invention has finally determined the optimum treatment process of Long Turbine Blades with precipitation hardening of martensitic stainless steel (particularly 13Cr-8Ni-2.2Mo-1.1Al steel) on the basis of test, not only solved because of residual austenite do not change the problem of the low strength cause fully, make intensity, plasticity and the toughness of this steel reach matched well; And a kind of thinking and method of new optimization heat treatment of workpieces technique are provided.
Applicant's statement, the present invention illustrates detailed process equipment and process flow process of the present invention by above-described embodiment, but the present invention is not limited to above-mentioned detailed process equipment and process flow process, does not mean that namely the present invention must rely on above-mentioned detailed process equipment and process flow process and could implement.The person of ordinary skill in the field should understand, any improvement in the present invention is to the interpolation of the equivalence replacement of each raw material of product of the present invention and ancillary component, the selection of concrete mode etc., within all dropping on protection scope of the present invention and open scope.
Claims (10)
1. the thermal treatment process of a martensitic precipitation comprises the following steps:
(1) solution treatment, cooling;
(2) ice-cold processing: temperature-5 ~ 2 ℃, at least 1 hour;
(3) ageing treatment.
2. technique as claimed in claim 1, is characterized in that, described martensitic precipitation is the 13Cr-8Ni-2.2Mo-1.1Al steel;
Preferably, described solid solution temperature is 900 ℃ ~ 1040 ℃, more preferably 910 ~ 950 ℃, and particularly preferably 925 ℃;
Preferably, the described solution treatment time is at least 0.5 hour, is particularly preferably at least 1 hour.
3. technique as claimed in claim 1 or 2, is characterized in that, after described solution treatment, cooling terminal point is below 20 ℃, more preferably below 18 ℃, is particularly preferably below 16 ℃;
Preferably, after described solution treatment, the type of cooling is air-cooled.
4. as the described technique of claim 1-3 any one, it is characterized in that, described ice-cold treatment temp is-2 ~ 1 ℃, is particularly preferably 0 ~ 1 ℃; Preferably, described ice-cold processing is carried out in frozen water;
Preferably, the described ice-cold treatment time is at least 2 hours.
5. as the described technique of claim 1-4 any one, it is characterized in that, cooling after described ice-cold processing; Preferably, after described ice-cold processing, cooling terminal point is room temperature; Preferably, be cooled to air cooling after described ice-cold processing.
6. as the described technique of claim 1-5 any one, it is characterized in that, described aging temperature is 520 ~ 570 ℃, more preferably 530 ~ 550 ℃, is particularly preferably 530 ~ 535 ℃;
Preferably, the described ageing treatment time is at least 2 hours, more preferably at least 3 hours, is particularly preferably at least 4 hours;
Preferably, cooling after described ageing treatment; Preferably, after described ageing treatment, cooling terminal point is room temperature; Preferably, be cooled to air cooling after described ageing treatment.
7. a martensitic precipitation, is characterized in that, described martensitic precipitation is obtained by the described thermal treatment process of claim 1-6 any one.
8. the purposes of a martensitic precipitation as claimed in claim 7, is characterized in that, described martensitic precipitation can be used as Long Turbine Blades.
9. a 13Cr-8Ni-2.2Mo-1.1Al steel, is characterized in that, described 13Cr-8Ni-2.2Mo-1.1Al steel is obtained by the described thermal treatment process of claim 1-6 any one.
10. the purposes of a 13Cr-8Ni-2.2Mo-1.1Al steel as claimed in claim 9, is characterized in that, described 13Cr-8Ni-2.2Mo-1.1Al steel is as the Long Turbine Blades of airway length greater than 1.2m.
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Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103667643A (en) * | 2013-12-12 | 2014-03-26 | 无锡透平叶片有限公司 | Heat treatment process for improving strength of PH13-8Mo stainless steel material |
| CN104178614A (en) * | 2014-09-02 | 2014-12-03 | 湘电集团有限公司 | Ultrahigh strengthening and toughening heat treatment method for low-carbon and high-alloy chromium nickel molybdenum aluminum stainless steel |
| CN105349747A (en) * | 2015-11-19 | 2016-02-24 | 哈尔滨工业大学 | Precipitation hardening stainless steel PH17-4 negative temperature gradient aging heat treatment method |
| CN105648172A (en) * | 2014-11-14 | 2016-06-08 | 陕西飞机工业（集团）有限公司 | Heat treatment process method for 0Cr13Ni8Mo2Al steel |
| CN106167850A (en) * | 2016-08-30 | 2016-11-30 | 陕西千山航空电子有限责任公司 | A kind of 23Co14ni12cr3mo Heat-Treatment of Steel method |
| CN110293287A (en) * | 2019-07-16 | 2019-10-01 | 安徽马钢工程技术集团有限公司 | A kind of welding procedure of superhigh intensity precipitation-hardening stainless steel |
| CN110564918A (en) * | 2019-09-29 | 2019-12-13 | 无锡市锡西化机配件有限公司 | Solution heat treatment process for stainless steel |
| CN110628997A (en) * | 2019-10-25 | 2019-12-31 | 贵州航天新力铸锻有限责任公司 | Heat treatment method for improving yield ratio of low-carbon martensite precipitation hardening stainless steel |
| CN110669905A (en) * | 2019-10-29 | 2020-01-10 | 贵州航天新力铸锻有限责任公司 | Heat treatment method for improving strength, toughness and mechanical property uniformity of bar |
| CN112553415A (en) * | 2020-12-04 | 2021-03-26 | 上海交通大学 | Clean graded quenching method for 0Cr16Ni5Mo1 martensitic stainless steel |
| CN113444859A (en) * | 2021-06-22 | 2021-09-28 | 北京航空航天大学 | Double tempering treatment process method for 10Cr13Co13Mo5Ni3W1VE ultrahigh-strength stainless steel product |
| WO2021254028A1 (en) * | 2020-06-17 | 2021-12-23 | 大连理工大学 | B2 nanoparticle coherent precipitation strengthened ultrahigh-strength maraging stainless steel and preparation method therefor |
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103667643A (en) * | 2013-12-12 | 2014-03-26 | 无锡透平叶片有限公司 | Heat treatment process for improving strength of PH13-8Mo stainless steel material |
| CN104178614A (en) * | 2014-09-02 | 2014-12-03 | 湘电集团有限公司 | Ultrahigh strengthening and toughening heat treatment method for low-carbon and high-alloy chromium nickel molybdenum aluminum stainless steel |
| CN105648172A (en) * | 2014-11-14 | 2016-06-08 | 陕西飞机工业（集团）有限公司 | Heat treatment process method for 0Cr13Ni8Mo2Al steel |
| CN105349747A (en) * | 2015-11-19 | 2016-02-24 | 哈尔滨工业大学 | Precipitation hardening stainless steel PH17-4 negative temperature gradient aging heat treatment method |
| CN106167850A (en) * | 2016-08-30 | 2016-11-30 | 陕西千山航空电子有限责任公司 | A kind of 23Co14ni12cr3mo Heat-Treatment of Steel method |
| CN110293287B (en) * | 2019-07-16 | 2021-06-22 | 安徽马钢工程技术集团有限公司 | Welding process of ultrahigh-strength precipitation hardening stainless steel |
| CN110293287A (en) * | 2019-07-16 | 2019-10-01 | 安徽马钢工程技术集团有限公司 | A kind of welding procedure of superhigh intensity precipitation-hardening stainless steel |
| CN110564918A (en) * | 2019-09-29 | 2019-12-13 | 无锡市锡西化机配件有限公司 | Solution heat treatment process for stainless steel |
| CN110628997A (en) * | 2019-10-25 | 2019-12-31 | 贵州航天新力铸锻有限责任公司 | Heat treatment method for improving yield ratio of low-carbon martensite precipitation hardening stainless steel |
| CN110669905A (en) * | 2019-10-29 | 2020-01-10 | 贵州航天新力铸锻有限责任公司 | Heat treatment method for improving strength, toughness and mechanical property uniformity of bar |
| WO2021254028A1 (en) * | 2020-06-17 | 2021-12-23 | 大连理工大学 | B2 nanoparticle coherent precipitation strengthened ultrahigh-strength maraging stainless steel and preparation method therefor |
| CN112553415A (en) * | 2020-12-04 | 2021-03-26 | 上海交通大学 | Clean graded quenching method for 0Cr16Ni5Mo1 martensitic stainless steel |
| CN113444859A (en) * | 2021-06-22 | 2021-09-28 | 北京航空航天大学 | Double tempering treatment process method for 10Cr13Co13Mo5Ni3W1VE ultrahigh-strength stainless steel product |
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Application publication date: 20130515 |