CN107537860A - Using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel - Google Patents
Using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel Download PDFInfo
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- CN107537860A CN107537860A CN201610493574.6A CN201610493574A CN107537860A CN 107537860 A CN107537860 A CN 107537860A CN 201610493574 A CN201610493574 A CN 201610493574A CN 107537860 A CN107537860 A CN 107537860A
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Abstract
The present invention discloses the method using cold rolling adjustment TP347H austenite heat-resistance structure of steel, make the deflection of TP347H austenitic heat-resistance steels generation at least 60% using cold-rolling process, α ' martensites are formed in this course and quantity is continuously increased, ε martensites quantity is reduced, and shows the lifting of microhardness and mechanical property.
Description
Technical field
The invention belongs to 18Cr-8Ni austenitic heat-resistance steel production technical fields, more specifically, more particularly to one kind is adopted
With the method for different distortion amount cold rolling adjustment austenite structure.
Background technology
TP347H austenitic heat-resistance steels are to add one on the basis of traditional 18-8 (1Cr19Ni11Nb) type austenitic steel
Quantitative Nb, the heat resistance of steel is improved in disperse educt Nb (C, N) mode, be in traditional 18-8 austenitic steels combination property compared with
One of strong heat resisting steel, it is applied to the Superheater tube of 600MW supercritical units.By the raising of Cr and Ni contents, make
Steel have preferable plasticity and toughness, excellent thermal structure stability, stronger oxidation resistance in steam energy and flue gas corrosion performance, compared with
Good welding performance and the production cost of relative moderate, but TP347H is single-phase austenite structure, plasticity and toughness it is excellent and
Insufficient strength it is high, it is necessary to reference to TP347H process of manufacture, study a kind of simple and easy improved method.
The content of the invention
It is resistance to using cold rolling adjustment TP347H austenites it is an object of the invention to overcome the deficiencies of the prior art and provide one kind
The method of hot structure of steel, realize a certain amount of α ' martensitic structures (α ' is introduced in single phase austenite matrix in this course
Martensitic structure has prominent intensity, but toughness is poor), TP347H is improved intensity while plasticity and toughness are kept, i.e., it is real
The comprehensive lifting of existing α ' martensites and austenite performance.
The technical purpose of the present invention is achieved by following technical proposals：
Using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel, cold rolling temperature is 15-30 degrees Celsius of room temperature,
It is preferred that 20-25 degrees Celsius, cold rolling reduction is at least 60%, preferably 60-90%.Cold rolling reduction refers in TP347H Ovshinskies
Deflection on body heat resisting steel thickness of sample direction, i.e., the ratio of the variable quantity of thickness and sample original depth after cold-rolling treatment
Value.
Tissue change of the TP347H austenitic heat-resistance steels in cold-rolled process is carried out using metallographic microscope, TEM, XRD
Characterize, it has been observed that deflection, during 0 → 30%, austenite slides along { 111 } face in TP347H, then dislocation
Sliding produces fault, and as deflection continues to increase, ε martensites initially form.During deflection 30 → 60%, ε martensites
Increasing number, while sliding meets with obstruction in crystal, produces a large amount of mechanical twins to coordinate ess-strain.Deflection 60 → 90%
During, α ' martensites are formed and quantity is continuously increased, and ε martensites quantity is reduced.TP347H austenitic heat-resistance steels become in cold rolling
Transformation mechanism of martensite under shape effect, as cold rolling reduction is from 15 → 90%, the. occurred successively is formed with γ (fcc)
→ ε (hcp), γ (fcc) → mechanical twin, ε (hcp) → α ' (bcc), γ (fcc) → α ' (bcc), pass through X ray
Diffraction is tested, and quantitative analysis is carried out to the content that α ' martensites are formed under different distortion amount.Changed by cold-rolling deformation
TP347H single phase austenite institutional framework, quantitatively introduces the second phase, during deflection 60 → 90%, α ' martensites formed and
Quantity is continuously increased, and α ' Martensite Volume Fractions reach 5% -35%, and now TP347H hardness and mechanical strength increase therewith
Add.
Technical scheme improves TP347H intensity by phase transformation strengthening.Before the excellent plasticity and toughness of TP347H are ensured
Put, control the content of cold rolling the second phase of institution adjustment, using the second phase high-strength characteristic, improve TP347H austenitic heat-resistance steels
Comprehensive mechanical property.
Brief description of the drawings
Fig. 1 is the metallographic structure photo of solid solution condition.
Fig. 2 is the metallographic structure photo of 30% cold rolling reduction sample.
Fig. 3 is the metallographic structure photo of 60% cold rolling reduction sample.
Fig. 4 is the metallographic structure photo of 90% cold rolling reduction sample.
Fig. 5 is the TEM photos of 30% cold rolling reduction sample.
Fig. 6 is the diffraction spot schematic diagram of border circular areas in Fig. 5.
Fig. 7 is the TEM photos of 60% cold rolling reduction sample.
Fig. 8 is the diffraction spot schematic diagram of border circular areas in Fig. 7.
Fig. 9 is the TEM photos of 90% cold rolling reduction sample.
Figure 10 is the diffraction spot schematic diagram of border circular areas in Fig. 9.
Figure 11 is the X ray diffracting spectrum of TP347H difference cold rolling reduction samples, wherein 1 is solid solution sample；2 be 30%
Cold rolling reduction sample；3 be 60% cold rolling reduction sample；4 be 90% cold rolling reduction sample.
Figure 12 is α ' Martensite Volume Fractions-cold rolling reduction curve map in TP347H difference cold rolling reduction samples.
Figure 13 is hardness-cold rolling reduction curve map of TP347H difference cold rolling reduction samples.
Embodiment
Technical scheme is further illustrated with reference to specific embodiment.
TP347H austenitic heat-resistance steels round steel is used as original material, by linear cutter 7 100 × 50 × 10 (mm,
Length × width × height) sample, by sample be put into Muffle furnace be heated to 1150 DEG C be incubated 30 minutes, rapid water cooling after coming out of the stove.
To be dissolved state TP347H austenitic heat-resistance steels carry out different distortion amount cold rolling trials (temperature is room temperature 20-25
Degree Celsius), every time deflection is 5% -15% (deformation of the deflection along on specimen height direction, i.e. through-thickness
Amount), per pass minor tick 10 minutes, 15%, 30%, 45%, 60%, 75% is obtained respectively, 90% deflection rolls plate, thickness side
Upward size is followed successively by 8.5mm, 7mm, 5.5mm, 4mm, 2.5mm, 1mm.
The element composition of TP347H austenitic heat-resistance steels
Using Japanese Olympus GX-FSL metallographic microscope, JEOL JEM-2100F transmission electron microscope,
The D8Advanced X-ray diffractometers of German Brooker and the MH-6L microhardness testers of Shanghai perseverance one, to above-mentioned preparation not
Sample with deflection is characterized.
From the metallographic microstructure photo of Fig. 1-4, solid solution sample is complete austenite structure；In 30% deflection
The austenite structure that sliding and fault occurs and a small amount of ε martensitic structures in sample be present；It is organic in 60% deflection sample
Austenite structure existing for tool twin structure and a large amount of ε martensitic structures, and also a small amount of α ' martensites start forming core；
A large amount of highdensity dislocations and the α ' martensitic structures of fragmentation be present in 90% deflection sample.Phase is revealed by the base tables of Fig. 5-10
Same variation tendency, the TEM tissues and diffraction spot of 30% cold rolling reduction sample, it is known that under this cold rolling reduction, sample
It is organized as face-centred cubic austenite and the ε martensites of six sides；The TEM tissues and diffraction spot of 60% cold rolling reduction sample, can
Know under this cold rolling reduction, sample tissue is austenite mechanical twin；The TEM of 90% cold rolling reduction sample is organized and spread out
Penetrate spot, it is known that under this cold rolling reduction, sample tissue is face-centred cubic austenite and body-centred cubic α ' martensites.
Material phase analysis is carried out using X-ray diffractometer, as shown figs. 11 and 12, is dissolved sample and 30% deflection sample
In the austenite peak that only exists, do not find the diffraction maximums of α ' martensites, the XRD diffracting spectrums of 60% deflection sample can be sent out
Now extremely weak fcc (110) peak, it is 5.4% to α ' Martensite Volume Fractions result of calculation, exists in 90% deflection sample obvious
Fcc (110) peak, the α ' Martensite Volume Fractions contained be 30.8%.Wherein α ' Martensite Volume Fractions calculate bibliography：
Dong-Seok Leem,Yong-Deuk Lee,Joong-Hwan Jun,and Chong-Sool Choi,Amount of
retained austenite at room temperature after reverse transformation of
Martensite to austenite in an Fe-13%Cr-7%Ni-3%Si martensitic stainless
steel,Scripta Materialia 45(2001)767-772。
α ' Martensite Volume Fraction calculation formula
As shown in figure 13, the microhardness of sample increases with the increase of cold rolling reduction, and solid solution sample Vickers hardness is
178HV, reach 473HV, the variation tendency of microhardness and the volume fraction of α ' martensites by 90% deflection Vickers hardness
Variation tendency is identical, illustrates that α ' martensite content increases lift the microhardness of sample.Under 20-25 degrees Celsius of sample room temperature
Tensile strength 580Mpa, yield strength 305Mpa, elongation percentage 51%；And with the increase of cold rolling reduction, show body force
Learn the enhancing of performance.
Exemplary description has been done to the present invention above, it should explanation, in the situation for the core for not departing from the present invention
Under, any simple deformation, modification or other skilled in the art can not spend the equivalent substitution of creative work equal
Fall into protection scope of the present invention.
Claims (9)
1. using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel, it is characterised in that cold rolling reduction is at least
60%.
2. the method according to claim 1 that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling, it is characterised in that
Cold rolling reduction is 60-90%.
3. the method according to claim 1 that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling, it is characterised in that
α ' Martensite Volume Fractions reach more than 5%.
4. the method according to claim 2 that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling, it is characterised in that
α ' Martensite Volume Fractions reach 5% -35%.
5. the method according to claim 1 that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling, it is characterised in that
In cold-rolled process, during deflection is from 0 to 30%, austenite occurs to slide in TP347H and dislocation, ε martensites start shape
Into；Deflection is by during 30 to 60%, ε martensite increasing numbers, while sliding meets with obstruction in crystal, and it is twin to produce machinery
It is brilliant；During deflection is from 60 to 90%, α ' martensites are formed and quantity is continuously increased, and ε martensites quantity is reduced.
6. the method that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling according to one of claim 1-5, it is special
Sign is that cold rolling temperature is 15-30 degrees Celsius, preferably 20-25 degrees Celsius.
7. the method that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling as described in one of claim 1-5 is being improved
Application in the hardness of TP347H austenitic heat-resistance steels.
8. the method that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling as described in one of claim 1-5 is being improved
Application in the mechanical property of TP347H austenitic heat-resistance steels.
9. the method that TP347H austenite heat-resistance structure of steel is adjusted using cold rolling as described in one of claim 1-5 is being controlled
Application in TP347H austenitic heat-resistance steels in α ' martensites amount of precipitation.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107868860A (en) * | 2016-09-26 | 2018-04-03 | 天津大学 | The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation |
| CN111705198A (en) * | 2020-06-08 | 2020-09-25 | 常州大学 | Production process method for improving corrosion resistance of TP347HFG steel seamless steel pipe |
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| US20080247902A1 (en) * | 2005-06-28 | 2008-10-09 | Piotr R. Scheller | High-Strength, Lightweight Austenitic-Martensitic Steel and the Use Thereof |
| CN102439188A (en) * | 2009-04-28 | 2012-05-02 | 现代制铁株式会社 | High manganese nitrogen-containing steel sheet having high strength and high ductility, and method for manufacturing same |
| CN103741066A (en) * | 2013-12-25 | 2014-04-23 | 宝钢不锈钢有限公司 | Non-magnetic hard austenitic stainless steel for precision electron and manufacturing method thereof |
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2016
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Patent Citations (3)
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| US20080247902A1 (en) * | 2005-06-28 | 2008-10-09 | Piotr R. Scheller | High-Strength, Lightweight Austenitic-Martensitic Steel and the Use Thereof |
| CN102439188A (en) * | 2009-04-28 | 2012-05-02 | 现代制铁株式会社 | High manganese nitrogen-containing steel sheet having high strength and high ductility, and method for manufacturing same |
| CN103741066A (en) * | 2013-12-25 | 2014-04-23 | 宝钢不锈钢有限公司 | Non-magnetic hard austenitic stainless steel for precision electron and manufacturing method thereof |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107868860A (en) * | 2016-09-26 | 2018-04-03 | 天津大学 | The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation |
| CN107868860B (en) * | 2016-09-26 | 2019-11-01 | 天津大学 | The method being precipitated using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel |
| CN111705198A (en) * | 2020-06-08 | 2020-09-25 | 常州大学 | Production process method for improving corrosion resistance of TP347HFG steel seamless steel pipe |
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Application publication date: 20180105 |