CN107868860B - The method being precipitated using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel - Google Patents
The method being precipitated using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel Download PDFInfo
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- CN107868860B CN107868860B CN201610854928.5A CN201610854928A CN107868860B CN 107868860 B CN107868860 B CN 107868860B CN 201610854928 A CN201610854928 A CN 201610854928A CN 107868860 B CN107868860 B CN 107868860B
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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
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
Abstract
The invention discloses a kind of methods being precipitated using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel, and cold rolling temperature is 15-30 degrees Celsius, and cold-rolling deformation is 30-90%.Application of the high-intensitive TP347H austenite steel and the above method prepared in aforementioned manners the invention also discloses one kind in the intensity for improving TP347H austenite steel.During cold deformation, NbC experienced dissolution, precipitation, broken and disperse educt transformation.Most NbC particle dissolves in 30% cold rolling reduction sample in solid solution state austenite crystal, while having strip NbC to be precipitated along austenite grain boundary, is broken for corynebacterium in being deformed into 60% sample later.As cold rolling reduction is increased to 90%, the nanoscale NbC particle of a large amount of Dispersed precipitates is precipitated in deformation induced martensite, improves the intensity of TP347H austenitic heat-resistance steel to 1418MPa from 552MPa.
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
Shape adjusts the method that niobium carbide is precipitated in TP347H austenitic steel.
Background technique
18Cr-8Ni austenitic steel has excellent corrosion resistance and plasticity and toughness, and TP347H austenitic heat-resistance steel is in 18Cr-
Certain content Nb element is added on 8Ni austenitic steel basis, improves material by the way that NbC is precipitated during hot environment is on active service
Creep-resistant property is widely used on the superheater and reheater piping of supercritical unit.The NbC of nano-scale exists
A large amount of during TP347H austenitic heat-resistance steel high-temperature aging to be formed, with the extension of aging time, quantity is continuously increased, ruler
Very little holding is stablized, and is main dispersion strengthening phase in TP347H austenitic heat-resistance steel.TP347H is single-phase austenite structure, modeling
Excellent tenacity and intensity is not high enough.
Summary of the invention
In view of the deficiencies of the prior art, TP347H austenite is adjusted using cold-rolling deformation it is an object of the invention to provide a kind of
The method that niobium carbide is precipitated in steel.
The method being precipitated using niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel, 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 austenite steel for being dissolved state progress multi-pass is rolled using double-roll rolling mill
System, the time interval rolled per pass are 3~5 minutes, and draught per pass is 1.5~2.5mm, so that the TP347H Ovshinsky
The deflection of body steel is 30~90%.
In the above-mentioned technical solutions, the deflection of the TP347H austenite steel is 30%, is dissolved in state austenite crystal
The NbC particle of strip is precipitated in austenite grain boundary in most of NbC grain dissolution；The deformation of the TP347H austenite steel
Amount is 60%, the NbC Particle Breakage of the strip at stub shape NbC particle；The deformation of the TP347H austenite steel
Amount is 90%, and the NbC Particle Breakage of the stub shape simultaneously dissolves, in deformation induced martensite disperse educt having a size of 30~
The NbC particle of 70nm.
A kind of high intensity TP347H austenite steel, prepares 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 austenite steel for being dissolved state is subjected to multi- pass rolling, depressed per pass
Amount is 1.5~2.5mm, so that the deflection of the TP347H austenite steel is 90%.
In the above-mentioned technical solutions, the deflection of the TP347H austenite steel reaches 90%, having a size of 30~70nm
NbC particle in deformation induced martensite disperse educt.
In the above-mentioned technical solutions, 1400~1500MPa of intensity average out to of prepared TP347H austenitic steel
As the above method is improving the application in TP347H austenite steel intensity.
In the above-mentioned technical solutions, the strength-enhancing amount of TP347H austenite steel is 400~900MPa.
Compared with the prior art, method of the invention carries out the cold rolling of different distortion amount to TP347H austenite (heat-resisting) steel
Test is developed using scanning electron microscope and the niobium carbide in transmission electron microscope observing difference cold-rolling deformation stage.During cold deformation,
NbC experienced dissolution, precipitation, broken and disperse educt transformation.Most NbC particle is 30% in solid solution state austenite crystal
It is dissolved in cold rolling reduction sample, while thering is strip NbC to be precipitated along austenite grain boundary, broken in being deformed into 60% sample later
Broken is corynebacterium.As cold rolling reduction is increased to 90%, the NbC particle of the nanoscale (30~70nm) of a large amount of Dispersed precipitates exists
It is precipitated in deformation induced martensite.Precipitation strength and the comprehensive function of processing hardening make the intensity of TP347H austenitic heat-resistance steel from
552MPa is improved to 1418MPa.
Detailed description of the invention
Fig. 1 is the preceding TP347H austenite steel X ray diffracting spectrum with Examples 1 to 3 of rolling；
Fig. 2 is the microstrain of the TP347H austenite steel of different cold rolling reductions；
Fig. 3 is the scanning electron microscope pattern (transgranular NbC particle) 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 be face-centred cubic Ovshinsky
The ε martensite of body and 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 particle of state, curve 2 are that TP347H austenite steel is made in embodiment 1, and curve 3 is
TP347H austenite steel is made in embodiment 2, and curve 4 is that TP347H austenite steel is made in embodiment 3.
Specific embodiment
In a specific embodiment of the invention, the instrument that test XRD is used is that Germany Brooker D8Advanced X is penetrated
Line diffractometer, the instrument that scanning pattern test uses is Hitachi, Japan s4800 scanning electron microscope, and the instrument that TEM is used is
Japan Electronics JEM-2100F transmission electron microscope, the instrument that tension test uses are the test of U.S. MTS C45 universal tensile
Machine.
The chemical component for being dissolved the TP347H austenite steel containing NbC particle of state is shown in Table 1.
Table 1: chemical component
With reference to the accompanying drawings and examples to niobium carbide in use cold-rolling deformation adjustment TP347H austenitic steel of the invention
The method of precipitation is described in detail.
It is by diameterSolid solution state the TP347H austenite steel containing NbC particle use linear cutter
It is the TP347H austenite steel sample of 65*20*10 (mm) at three block sizes, carries out cold rolling, cold rolling temperature for following embodiments
Degree is 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 rolled per pass 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 rolled per pass 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 rolled per pass 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 particle
TP347H austenite steel, curve 2 are the TP347H austenite steel (embodiment 1) that deflection is 30%, and curve 3 is deflection
For 60% TP347H austenite steel (embodiment 2), curve 4 is that the TP347H austenite steel that deflection is 90% (is implemented
Example 3).As shown in Figure 1, a large amount of deformation induced martensites are formed in TP347H austenite steel sample when deflection is 90%.
As shown in Figure 2, it is dissolved the microstrain of austenite lattice in the TP347H austenite steel containing NbC particle of state only
It is 0.2%, before deflection 60%, microstrain linearly gently increases to 0.5%, is increased in cold rolling reduction from 60%
During 90%, the microstrain of austenite lattice is increased rapidly to 1.45%.
Using scanning electron microscope and transmission electron microscope in the TP347H austenite steel of different distortion amount in Examples 1 to 3
NbC phase is observed, and includes a large amount of NbC in austenite crystal in the TP347H austenite steel of non-cold rolling as shown in fig. 3 to 7
Particle, grain boundaries do not have precipitate appearance.In the TP347H austenite steel that deflection is 30%, transgranular major part NbC is molten
Solution only retains the tiny NbC particle of a small amount of size, and strip NbC is precipitated in austenite grain boundary.It is 60% in deflection
In TP347H austenite steel, grain boundaries strip NbC is broken for corynebacterium.The TP347H austenitic steel for being 90% in deflection
In material, grain boundaries corynebacterium NbC fragmentation is fritter and gradually dissolves, the disperse in deformation induced martensite of nanoscale NbC particle
It is precipitated.
The larger-size NbC particle of TP347H austenite of solid solution state is dissolved since carbon atom diffuses at dislocation.
Dislocation slides plug product near crystal boundary along austenite { 111 } face, increases grain boundaries carbon concentration, NbC phase is immediately along Austria
Family name's body crystal boundary forming core and long greatly strip.Austenite grain deforms during subsequent deflection increases, and leads to crystal boundary
Director's bar shaped NbC is broken for corynebacterium.As cold rolling reduction continues to increase to 90%, austenite grain is crushed refinement in fibre
Shape is tieed up, grain boundaries corynebacterium NbC fragmentation is fritter and gradually dissolves.Large deformation induces austenite phase transformation and generates a large amount of α ' geneva
There is approximate symbiosis and epibiosis in body, { 200 } face of NbC phase and { 110 } face of α ' martensite, promote NbC of 30~70nm of nanoscale
Grain is precipitated at dislocation in α ' martensite.
Preceding to rolling and Examples 1 to 3 TP347H austenite steel carries out tensile sample, in different rolling reduction samples
It is 20mm that interception gauge length, which is 40mm sectional area, on product2Tensile sample, carry out tension test at 23 DEG C of temperature.By Fig. 8
It is found that the breaking strain of the TP347H austenite steel containing NbC particle of original undeformed 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, so that the intensity of material is improved nearly three times, this is because Dispersed precipitate
Nanoscale NbC particle and dislocation between reciprocation occurs, hinder dislocation motion, dislocation passes through nanoscale using bypass mechanism
NbC increases dislocation motion resistance, improves the resistance of deformation of material, improves TP347H austenite heat-resistance hardness of steel.
Illustrative description has been done to the present invention above, it should explanation, the case where not departing from core of the invention
Under, any simple deformation, modification or other skilled in the art can not spend the equivalent replacement of creative work equal
Fall into protection scope of the present invention.
Claims (2)
1. improving TP347H austenite steel using the method that niobium carbide in cold-rolling deformation adjustment TP347H austenitic steel is precipitated
Application in intensity, which is characterized in that cold rolling temperature is 15-30 degrees Celsius of room temperature；State will be dissolved using double-roll rolling mill
TP347H austenite steel carries out multi- pass rolling, and the time interval rolled per pass is 3 ~ 5 minutes, and draught per pass is
1.5 ~ 2.5 mm, so that the deflection of the TP347H austenite steel is 90%, the NbC Particle Breakage of stub shape simultaneously dissolves, In
NbC particle of the disperse educt having a size of 30 ~ 70 nm in deformation induced martensite, the intensity of prepared TP347H austenitic steel
1400 ~ 1500 MPa of average out to, the strength-enhancing amount of TP347H austenite steel are 400 ~ 900 MPa.
2. application according to claim 1, which is characterized in that cold rolling temperature is 20-25 degrees Celsius.
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| Publication number | Priority date | Publication date | Assignee | Title |
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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 |
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| Publication number | Priority date | Publication date | Assignee | Title |
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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 |
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