CN107868860A - The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation - Google Patents
The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation Download PDFInfo
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- CN107868860A CN107868860A CN201610854928.5A CN201610854928A CN107868860A CN 107868860 A CN107868860 A CN 107868860A CN 201610854928 A CN201610854928 A CN 201610854928A CN 107868860 A CN107868860 A CN 107868860A
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D6/005—Heat treatment of ferrous alloys containing Mn
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Abstract
The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation the invention discloses a kind of, cold rolling temperature is 15-30 degrees Celsius, and cold-rolling deformation is 30-90%.The invention also discloses a kind of application of high intensity TP347H austenites steel prepared in aforementioned manners and the above method in the intensity for improving TP347H austenite steel.During cold deformation, NbC experienced dissolving, precipitation, broken and disperse educt transformation.Most NbC particles dissolve in 30% cold rolling reduction sample in solid solution state austenite crystal, while have strip NbC to be separated out along austenite grain boundary, are broken for corynebacterium in 60% sample is deformed into afterwards.As cold rolling reduction is increased to 90%, the nano level NbC particles of a large amount of Dispersed precipitates separate out in deformation induced martensite, the intensity of TP347H austenitic heat-resistance steels is improved from 552MPa to 1418MPa.
Description
Technical field
The invention belongs to 18Cr-8Ni austenitic heat-resistance steel production technical fields, relate in particular to a kind of using cold rolling change
The method that niobium carbide separates out in shape adjustment TP347H austenitic steels.
Background technology
18Cr-8Ni austenitic steels have excellent corrosion resistance and plasticity and toughness, and TP347H austenitic heat-resistance steels are in 18Cr-
Certain content Nb elements are added on 8Ni austenitic steels basis, material is improved by separating out NbC during hot environment military service
Creep-resistant property, it is widely used on the superheater and reheater piping of supercritical unit.The NbC of nano-scale exists
Largely formed during TP347H austenitic heat-resistance steel high-temperature agings, with the extension of aging time, its quantity is continuously increased, chi
It is very little to keep stable, it is dispersion-strengtherning phase main in TP347H austenitic heat-resistance steels.TP347H is single-phase austenite structure, modeling
Tenacity excellent and insufficient strength is high.
The content of the invention
In view of the shortcomings of the prior art, it is an object of the invention to provide a kind of using cold-rolling deformation adjustment TP347H austenites
The method that niobium carbide separates out in steel.
The method that niobium carbide separates out in TP347H austenitic steels is adjusted using cold-rolling deformation, cold rolling temperature is room temperature 15-30
Degree Celsius, cold-rolling deformation is 30-90%.
In the above-mentioned technical solutions, cold rolling temperature is 20-25 degrees Celsius.
In the above-mentioned technical solutions, the TP347H austenites steel for being dissolved state are carried out into multi-pass using double-roll rolling mill to roll
System, the time interval of every time rolling is 3~5 minutes, and draught per pass is 1.5~2.5mm, so that the TP347H Ovshinskies
The deflection of body steel is 30~90%.
In the above-mentioned technical solutions, the deflection of the TP347H austenites steel is 30%, is dissolved in state austenite crystal
Most of NbC grain dissolutions, the NbC particles of strip are separated out in austenite grain boundary；The deformation of the TP347H austenites steel
Measure as 60%, the NbC particles of the NbC Particle Breakages of the strip into stub shape；The deformation of the TP347H austenites steel
Measure as 90%, the NbC Particle Breakages of the stub shape simultaneously dissolve, in deformation induced martensite disperse educt size be 30~
70nm NbC particles.
A kind of high intensity TP347H austenite steel, are prepared by the following method：Cold rolling temperature is that room temperature 15-30 is Celsius
Degree, cold-rolling deformation 90%.
In the above-mentioned technical solutions, the TP347H austenites steel for being dissolved state are subjected to multi- pass rolling, every time pressure
Measure as 1.5~2.5mm, so that the deflection of the TP347H austenites steel is 90%.
In the above-mentioned technical solutions, the deflection of the TP347H austenites steel reaches 90%, and size is 30~70nm
NbC particles in deformation induced martensite disperse educt.
In the above-mentioned technical solutions, 1400~1500MPa of intensity average out to of prepared TP347H austenitic steels
Such as application of the above-mentioned method in TP347H austenite steel strengths are improved.
In the above-mentioned technical solutions, the strength-enhancing amount of TP347H austenites steel is 400~900MPa.
Compared to prior art, method of the invention carries out the cold rolling of different distortion amount to TP347H austenites (heat-resisting) steel
Experiment, developed using ESEM and the niobium carbide in transmission electron microscope observing difference cold-rolling deformation stage.During cold deformation,
NbC experienced dissolving, precipitation, broken and disperse educt transformation.Most NbC particles are 30% in solid solution state austenite crystal
Dissolved in cold rolling reduction sample, while there is strip NbC to be separated out along austenite grain boundary, broken afterwards in 60% sample is deformed into
Broken is corynebacterium.As cold rolling reduction is increased to 90%, the NbC particles of the nanoscale (30~70nm) of a large amount of Dispersed precipitates exist
Separated out in deformation induced martensite.The comprehensive function of precipitation strength and processing hardening make the intensity of TP347H austenitic heat-resistance steels from
552MPa is improved to 1418MPa.
Brief description of the drawings
Fig. 1 is the preceding TP347H austenite steel X ray diffracting spectrums with embodiment 1~3 of rolling；
Fig. 2 is the microstrain of the TP347H austenite steel of different cold rolling reductions；
Fig. 3 is the ESEM pattern (transgranular NbC particles) of the TP347H austenite steel before rolling；
Fig. 4 is the scanning pattern of the TP347H austenite steel of 30% cold rolling reduction；
Fig. 5 is the scanning pattern of the TP347H austenite steel of 60% cold rolling reduction；
Fig. 6 is the scanning pattern of the TP347H austenite steel of 90% cold rolling reduction；
Fig. 7 be the TP347H austenite steel of 30% cold rolling reduction TEM tissue (diffraction spot is face-centred cubic Ovshinsky
Body and the ε martensites of six sides)
Fig. 8 is the stress-strain diagram of the TP347H austenite steel of different cold rolling reductions, wherein, curve 1 is solid solution
The TP347H austenite steel containing NbC particles of state, curve 2 are that TP347H austenite steel are made in embodiment 1, and curve 3 is
TP347H austenite steel are made in embodiment 2, and curve 4 is that TP347H austenite steel are made in embodiment 3.
Embodiment
In the embodiment of the present invention, the instrument that test XRD is used is penetrated for German Brooker D8Advanced X
Line diffractometer, the instrument that scanning pattern test uses is FDAC s4800 SEM, and the instrument that TEM is used is
JEOL's JEM-2100F transmission electron microscopes, the instrument that tension test uses are tested for U.S.'s MTS C45 universal tensiles
Machine.
The chemical composition for being dissolved the TP347H austenite steel containing NbC particles of state is shown in Table 1.
Table 1：Chemical composition
With reference to the accompanying drawings and examples to niobium carbide in the use cold-rolling deformation adjustment TP347H austenitic steels of the present invention
The method of precipitation is described in detail.
Will be a diameter ofThe TP347H austenites steel containing NbC particles of solid solution state use linear cutter
Into the TP347H austenite steel samples that three block sizes are 65*20*10 (mm), cold rolling, cold rolling temperature are carried out for following embodiments
Spend for 20 degrees Celsius of room temperature.
Embodiment 1
TP347H austenite steel sample is carried out by multi-pass cold rolling using double-roll rolling mill, so that TP347H austenite steel
The deflection of sample is 30%, and the time interval of every time rolling is 5 minutes, and draught per pass is 1.5mm.
Embodiment 2
TP347H austenite steel sample is carried out by multi-pass cold rolling using double-roll rolling mill, so that TP347H austenite steel
The deflection of sample is 60%, and the time interval of every time rolling is 5 minutes, and draught per pass is 1.5mm.
Embodiment 3
TP347H austenite steel sample is carried out by multi-pass cold rolling using double-roll rolling mill, so that TP347H austenite steel
The deflection of sample is 90%, and the time interval of every time rolling is 5 minutes, and draught per pass is 1.5mm.
Material phase analysis is carried out using X-ray diffractometer, as shown in figure 1, curve 1 is solid solution state containing NbC particles
TP347H austenite steel, curve 2 are the TP347H austenites steel (embodiment 1) that deflection is 30%, and curve 3 is deflection
For 60% TP347H austenites steel (embodiment 2), curve 4 is that the TP347H austenites steel that deflection is 90% (are implemented
Example 3).As shown in Figure 1, a large amount of deformation induced martensites are formed in TP347H austenite steel samples when deflection is 90%.
As shown in Figure 2, it is dissolved the microstrain of austenite lattice in the TP347H austenite steel containing NbC particles of state only
For 0.2%, before deflection 60%, microstrain linearly gently increases to 0.5%, is brought up in cold rolling reduction from 60%
During 90%, the microstrain of austenite lattice is increased rapidly to 1.45%.
Using ESEM and transmission electron microscope in the TP347H austenite steel of different distortion amount in embodiment 1~3
NbC phases are observed, and as shown in fig. 3 to 7, in the TP347H austenite steel of non-cold rolling, a large amount of NbC are included in austenite crystal
Particle, grain boundaries do not have precipitate appearance.In the TP347H austenite steel that deflection is 30%, transgranular most of NbC is molten
Solution, only retain the tiny NbC particles of a small amount of size, and strip NbC is separated out in austenite grain boundary.It is 60% in deflection
In TP347H austenite steel, grain boundaries strip NbC is broken for corynebacterium.In the TP347H austenitic steels that deflection is 90%
In material, grain boundaries corynebacterium NbC fragmentations are fritter and gradually dissolved, the disperse in deformation induced martensite of nanoscale NbC particles
Separate out.
The larger-size NbC particles of TP347H austenites of solid solution state are dissolved because carbon atom is diffused at dislocation.
Dislocation slides plug product near crystal boundary along austenite { 111 } face, raises grain boundaries carbon concentration, NbC phases are immediately along Austria
Family name's body crystal boundary forming core and long greatly strip.Austenite crystal deforms during the increase of subsequent deflection, causes crystal boundary
Director's bar shaped NbC is broken for corynebacterium.As cold rolling reduction continues to increase to 90%, austenite crystal is crushed refinement in fibre
Shape is tieed up, grain boundaries corynebacterium NbC fragmentations are fritter and gradually dissolved.Large deformation induces austenite phase transformation and produces a large amount of α ' geneva
There is approximate symbiosis and epibiosis in body, { 200 } face of NbC phases and { 110 } face of α ' martensites, promote NbC of 30~70nm of nanoscale
Grain separates out in α ' martensites at dislocation.
Tensile sample is carried out to the TP347H austenites steel for rolling preceding and embodiment 1~3, in different rolling reduction samples
It is that 40mm sectional areas are 20mm that gauge length is intercepted on product2Tensile sample, carry out tension test at 23 DEG C of temperature.By Fig. 8
Understand, the breaking strain of the TP347H austenite steel containing NbC particles of original not deformed solid solution state is up to 86%, and tension
Intensity is only 552Mpa, and with the continuous increase of cold rolling reduction, the tensile strength of sample is gradually increasing.When cold rolling reduction reaches
To 90%, the tensile strength of sample reaches 1418Mpa, the intensity of material is improved nearly three times, this is due to Dispersed precipitate
Nanoscale NbC particles and dislocation between reciprocation occurs, hinder dislocation motion, dislocation passes through nanoscale using bypass mechanism
NbC, increase dislocation motion resistance, improve the resistance of deformation of material, improve TP347H austenite heat-resistances hardness of steel.
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 (10)
1. the method separated out using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steels, it is characterised in that cold rolling temperature is
15-30 degrees Celsius of room temperature, cold-rolling deformation are 30-90%.
2. according to claim 1 adjust the method that niobium carbide separates out in TP347H austenitic steels using cold-rolling deformation, its
It is characterised by, cold rolling temperature is 20-25 degrees Celsius.
3. according to claim 1 adjust the method that niobium carbide separates out in TP347H austenitic steels using cold-rolling deformation, its
Be characterised by, using double-roll rolling mill will be dissolved state TP347H austenites steel carry out multi- pass rolling, every time rolling when
Between at intervals of 3~5 minutes, draught per pass is 1.5~2.5mm, so that the deflection of the TP347H austenites steel is
30~90%.
4. according to claim 1 adjust the method that niobium carbide separates out in TP347H austenitic steels using cold-rolling deformation, its
It is characterised by, the deflection of the TP347H austenites steel is 30%, and it is molten to be dissolved most of NbC particles in state austenite crystal
Solution, the NbC particles of strip are separated out in austenite grain boundary；The deflection of the TP347H austenites steel is 60%, the length
NbC particle of the NbC Particle Breakages of bar shaped into stub shape；The deflection of the TP347H austenites steel is 90%, described short
The NbC Particle Breakages of rod simultaneously dissolve, and disperse educt size is 30~70nm NbC particles in deformation induced martensite.
5. a kind of high intensity TP347H austenite steel, it is characterised in that prepare by the following method：Cold rolling temperature is room temperature
15-30 degrees Celsius, cold-rolling deformation 90%.
6. high intensity TP347H austenite steel according to claim 5, it is characterised in that the TP347H for being dissolved state is difficult to understand
Family name's body steel carry out multi- pass rolling, and draught per pass is 1.5~2.5mm, so that the change of the TP347H austenites steel
Shape amount is 90%.
7. high intensity TP347H austenite steel according to claim 5, it is characterised in that the TP347H austenitic steels
The deflection of material reaches 90%, the NbC particles that size is 30~70nm disperse educt in deformation induced martensite.
8. high intensity TP347H austenite steel according to claim 5, it is characterised in that prepared TP347H austenites
1400~1500MPa of intensity average out to of steel.
9. application of the method in TP347H austenite steel strengths are improved as described in one of claim 1-4.
10. application according to claim 9, it is characterised in that the strength-enhancing amount of TP347H austenite steel be 400~
900MPa。
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113584263A (en) * | 2021-07-26 | 2021-11-02 | 安徽工业大学 | Method for eliminating mixed crystals in S31035 high-alloy austenitic heat-resistant steel |
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|---|---|---|---|---|
| CN102363870A (en) * | 2011-10-10 | 2012-02-29 | 刘群联 | Austenitic stainless steel for manufacturing steel tube and manufacturing method thereof |
| CN105177262A (en) * | 2015-09-25 | 2015-12-23 | 安阳工学院 | Method for increasing proportion of special grain boundaries in precipitation strengthened austenitic heat-resistance steel |
| CN107537860A (en) * | 2016-06-25 | 2018-01-05 | 天津大学 | Using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel |
| US20180142334A1 (en) * | 2015-06-15 | 2018-05-24 | Nippon Steel & Sumitomo Metal Corporation | HIGH Cr-BASED AUSTENITIC STAINLESS STEEL |
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- 2016-09-26 CN CN201610854928.5A patent/CN107868860B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102363870A (en) * | 2011-10-10 | 2012-02-29 | 刘群联 | Austenitic stainless steel for manufacturing steel tube and manufacturing method thereof |
| US20180142334A1 (en) * | 2015-06-15 | 2018-05-24 | Nippon Steel & Sumitomo Metal Corporation | HIGH Cr-BASED AUSTENITIC STAINLESS STEEL |
| CN105177262A (en) * | 2015-09-25 | 2015-12-23 | 安阳工学院 | Method for increasing proportion of special grain boundaries in precipitation strengthened austenitic heat-resistance steel |
| CN107537860A (en) * | 2016-06-25 | 2018-01-05 | 天津大学 | Using the method for cold rolling adjustment TP347H austenite heat-resistance structure of steel |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113584263A (en) * | 2021-07-26 | 2021-11-02 | 安徽工业大学 | Method for eliminating mixed crystals in S31035 high-alloy austenitic heat-resistant steel |
| CN113584263B (en) * | 2021-07-26 | 2022-06-21 | 安徽工业大学 | Method for eliminating mixed crystals in S31035 high-alloy austenitic heat-resistant steel |
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