CN106399833B - The middle chromium of extremely low brittle transition temperature is without molybdenum ferritic stainless steel and preparation method thereof - Google Patents
The middle chromium of extremely low brittle transition temperature is without molybdenum ferritic stainless steel and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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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
- C21D1/26—Methods of annealing
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
A kind of middle chromium of extremely low brittle transition temperature contains C 0.005~0.015%, N 0.005~0.015% by mass percentage without molybdenum ferritic stainless steel and preparation method thereof, composition, Si≤0.5%, Mn≤0.2%, P≤0.03%, S≤0.01%, O≤0.005%, Cr 18~22%, Nb 0.08~0.18%, Ti 0.05~0.1%, Ni 0.2~0.4%, Al 0.1~0.2%, Cu 0.3~0.5%, surplus are iron and inevitable impurity, and brittle transition temperature is at 120~100 DEG C；Preparation method is：（1）Smelt and pour into a mould in vacuum induction melting furnace；（2）1000~1200 DEG C of 60~150min of insulation are heated to, then hot rolling, accumulation drafts is 96~98%；（3）850~950 DEG C are heated to, is incubated 6~8min.The inventive method improves its service life and security under the harsh Service Environment such as low temperature, reduces the production cost of steel, finally realize stainless steel production economize on resources, energy-saving and emission-reduction and the target such as prevent the pollution of the environment.
Description
Technical field
The invention belongs to metallurgical technology field, more particularly to a kind of middle chromium of extremely low brittle transition temperature without molybdenum-iron ferritic not
Become rusty steel and preparation method thereof.
Background technology
Ferritic stainless steel refers to body-centered cubic crystal structure, high temperature and room temperature be respectively provided with complete ferrite or with
Ferrite is agent structure, and its Cr content is more than a series of 10.5% ferrous alloys, in order to assign such alloy some specificities
Can, also it is commonly incorporated into the elements such as appropriate Mo, Ni, Al, Cu, Nb, Ti or Nb+Ti.By the Cr contents in steel can be divided into low chromium, in
Chromium and the class of high chromium content ferrite stainless steel three.Fe-Cr systems ferritic stainless steel and Fe- can be divided into by being formed by the alloying element in steel
The class of Cr-Mo systems ferritic stainless steel two.
Ferritic stainless steel in addition to good rustless property and resistance to general corrosion performance, its resistance to chloride stress corrosion,
The function admirable such as resistance to spot corrosion and slit and corrosion resistant.Compared with chromiumnickel austenite stainless steel, ferritic stainless steel is not nickeliferous or only contains
A small amount of nickel, thus be one kind without nickel and save nickel and stainless steel.Ferrite stainless hardness of steel is high, and low, heat conduction system is inclined in cold work hardening
Number is the 130~150% of austenitic stainless steel, and linear expansion coefficient is only the 60~70% of austenitic stainless steel, and has magnetic.Just
It is due to that ferritic stainless steel has these unique advantages, in household electrical appliance, kitchen utensils, communications and transportation, building decoration, sea
The civilian and industrial circles such as water desalination, petroleum refining, basic industry, nuclear energy and naval vessel have broad application prospects.
But since ferritic stainless steel in 1912 comes out, compared with chromiumnickel austenite stainless steel, Yield comparison it is low and
Purposes is subject to many limitations, and this and ferritic stainless steel, particularly chrome content have brittle transition temperature when being more than 16% still needs and change
It is closely related with shortcoming to be apt to this deficiency.This deficiency and shortcoming outstanding behaviours exist, on the one hand, with chromiumnickel austenite stainless steel phase
Than the brittle transition temperature of ferritic stainless steel is high.This has one with the crystal structure of ferritic stainless steel and compared with high-Cr
Fixed contact.Compared with Face-centred Cubic Metals, slide surface atomic arrangement density is small in body-centered cubic ferrite stainless steel, slide surface face
Spacing is small, and adhesion is strong between face and face；Glide direction number is few, and atomic density is small in glide direction, former in those directions
Sub- spacing is big, and the Bai Shi vectors of dislocation are big；Cr atoms suppress starting for some slip systems.This causes skid resistance to increase, and becomes
Shape harmony reduces, and beneficial to the germinating and extension of sharp crack, ultimately causes brittle break and reduces brittle transition temperature.And
And this deteriorating effects showed under low-temperature condition it is particularly evident.On the other hand, the brittle transition temperature pair of ferritic stainless steel
Steel plate thickness is very sensitive, that is, thickness effect be present.That is, steel plate is thicker, brittle transition temperature is higher.For example, for
Chrome ferritic stainless steel 439 is when thickness reaches 5~6mm in common, its corresponding brittle transition temperature just reach room temperature and with
On；And when thickness reaches 8mm, brittle transition temperature will be far above room temperature, as shown in Figure 1.This thickness effect exists with material
Stress state in impact process residing for different-thickness sample sizes breach tip is related.In impact process, work as thinner thickness
When, breach tip place, substantially can be with Free Transform perpendicular to thickness of slab direction, stress state generally two be being answered to the plane of stretching
Power state；When thickness increase, at breach tip, suffered restraints in the deformation perpendicular to thickness of slab direction, stress state is three-dimensional
Stress state；In addition, the plastic deformation to suffer restraints will promote the generation of Transition of Brittleness.Therefore, when steel plate thickness increase, fragility
Transition temperature increase.This Special Manifestations are just seriously govern the application of ferritic stainless steel, especially under extremely cold environment, and
Applied thickness when further limit ferritic stainless steel as structural material, direct applied thickness, which should be limited in, to be no more than
6mm。
At present, both at home and abroad many scholars the performance improvement with regard to ferritic stainless steel and its manufacture method propose it is multinomial specially
Profit.Japan Patent JP63-219551A discloses a kind of ferritic stainless steel with preferable low-temperature flexibility, that is, passes through addition 0.2
~0.8% Ni come obtain the chromium content with preferable low-temperature flexibility be 11~18% ferritic stainless steel.With original technology phase
Than the brittle transition temperature of the ferritic stainless steel of invention is below -80 DEG C.However, can from the embodiment of above-mentioned patent
It was found that for the ferritic stainless steel that chromium content is 18.1%, although the Ni of addition 0.53%, brittle transition temperature is only -3
DEG C, show that this patent is not controlled for the brittle transition temperature for the ferritic stainless steel cut deal that chromium content is more than 18%
System and improvement.Japan Patent JP2008-189974A discloses a kind of automobile row with preferable thermal fatigue property and low-temperature flexibility
Gas system ferritic stainless steel, i.e., obtained by the Nb of addition 0.5~0.7%, 0.05~0.3% Ti and 1~2% Cu
Automobile exhaust system chromium content with preferable thermal fatigue property and low-temperature flexibility is 10~20% ferritic stainless steel.But
Be the brittle transition temperature that invention ferritic stainless steel can be found from the embodiment of above-mentioned patent only up to less than -25 DEG C,
Certain gap compared with less than -100 DEG C of brittle transition temperature also be present.And above-mentioned patent is mainly for automobile exhaust system
Use ferritic stainless steel（Thickness is no more than 5.0mm）Performance be controlled and improve, not for thickness in more than 5mm
The brittle transition temperature of ferritic stainless steel cut deal be controlled and improve.European patent EP 0478790A1 discloses one
Kind with preferable low-temperature flexibility, weldability and heat resistance heatproof ferrite stainless steel, i.e., by control Mn/S >=200, Nb >=
0.2+8（C+N）And the index such as Ni+Cu≤4% obtains the automobile exhaust system with preferable low-temperature flexibility, weldability and heat resistance
System chromium content is 17~25% Fe-Cr-Mo systems ferritic stainless steel.However, it can be found from the embodiment of above-mentioned patent
Bright ferritic stainless steel (thickness：4.5mm）30~80% under the conditions of being about 25 DEG C in the impact flexibility under the conditions of -25 DEG C.Root
According to the regulation of brittle transition temperature in GB/T 229-2007, the brittle transition temperature of the ferritic stainless steel of foregoing invention close to-
25 DEG C, fail to promote ferritic stainless steel brittle transition temperature be down to it is extremely low（Less than -100 DEG C）.This will be difficult to meet iron element
Body stainless steel cut deal under cold conditions, the requirement of especially extremely cold environment.Moreover, above-mentioned patent is not directed to Fe-
Cr systems ferritic stainless steel cut deal mechanical property, especially brittle transition temperature are controlled and improved.
Chinese patent CN101168822A discloses a kind of manufacture method of high ductility nickel-free ferrite stainless steel, that is, passes through
Addition 0.02~0.1% rare earth element come improve chromium content be 16~20% ferritic stainless steel room temperature and low-temperature flexibility,
And the impact flexibility for the ferritic stainless steel for pointing out to invent under the conditions of -20 DEG C, 0 DEG C and 20 DEG C is up to about the 5 of original technology
Times.But it can find that impact flexibility of the ferritic stainless steel of invention under the conditions of 20 DEG C is from the embodiment of above-mentioned patent
32~130J/cm2, ballistic work is 25.6~104J；Impact flexibility under the conditions of -20 DEG C is 15~50J/cm2, ballistic work is
12~40J, less than 50% under the conditions of 20 DEG C.According to the regulation of brittle transition temperature in GB/T 229-2007, it may be determined that
The brittle transition temperature of the ferritic stainless steel of foregoing invention fails to promote the fragility of ferritic stainless steel substantially close to -20 DEG C
Transition temperature is down to extremely low（Less than -100 DEG C）.This will be difficult to meet ferritic stainless steel under cold conditions, especially extremely cold
The requirement of environment.Moreover, this patent and being not added with Nb, Ti, Ni, Al and Cu.Chinese patent CN105051234A is disclosed
A kind of ferrite-group stainless steel hot rolled steel plate and its manufacture method and steel band, i.e., by composition design and annealing process control come
Improve the toughness and corrosion resistance for the ferritic stainless steel that chromium content is 14~18%, compared with original technology, the ferrite of invention is not
Become rusty steel（Thickness：5.0~9.0mm）Impact flexibility under the conditions of 0 DEG C is in 10J/cm2More than.However, the reality from above-mentioned patent
Applying in example to find, for the ferritic stainless steel that chromium content is 20.1%, although remaining alloying element content is advised in this patent
Determine in scope, but its impact flexibility under the conditions of 0 DEG C is less than 10J/cm2, it is not 18% for chromium content to show this patent
The brittle transition temperature of ferritic stainless steel cut deal above is controlled and improved.Chinese patent CN104195451A is disclosed
A kind of middle chrome ferritic stainless steel and its manufacture method, that is, pass through composition design and hot rolling, hot-roll annealing, cold rolling, cold rolling
After annealing and batch etc. technology controlling and process come improve the obdurability for the middle chrome ferritic stainless steel that chromium content is 16.5~19.5%,
Corrosion resistance and impact.But above-mentioned patent and Cu being not added with, Mn contents are high, and Al content is low, and invention ferritic stainless steel
Manufacturing process it is complex（Except hot rolling, hot-roll annealing is used, also need using cold rolling, cold rolling after annealing etc.）.Chinese patent
The method that CN102643968A discloses plate toughness in chrome ferritic stainless steel in a kind of raising.I.e. by introduce warm-rolling technique with
The tissue of fining ferrite stainless steel simultaneously optimizes Grain Boundary Character distribution to improve the toughness of ferritic stainless steel.It is however, above-mentioned special
Profit is simultaneously not added with Ni, Al and Cu, and the manufacturing process of invention ferritic stainless steel is complex（Except use hot rolling and annealing,
Rolling deformation etc. need to be also carried out in 260~600 DEG C of temperature ranges）.
Chinese patent CN102605262A discloses a kind of ferritic stainless steel and its manufacture method, i.e., by add V and
Nb simultaneously uses appropriate Technology for Heating Processing tough for the impact of 17~20% Fe-Cr-Mo systems ferritic stainless steel to improve chromium content
Property and brittle transition temperature.However, it can be found from the embodiment of above-mentioned patent, compared with original technology, although foregoing invention
Fe-Cr-Mo systems ferritic stainless steel brittle transition temperature (thickness：5.0mm）About 60 DEG C of highest reduction, but its fragility
Transition temperature still at 0 DEG C or so, fail to promote ferritic stainless steel brittle transition temperature be down to it is extremely low（Less than -100 DEG C）.This
Ferritic stainless steel will be difficult to meet under cold conditions, the requirement of especially extremely cold environment.Moreover, this patent is not
Ti and Cu is added, Al content is low, and fails to be controlled for the brittle transition temperature of Fe-Cr systems ferritic stainless steel cut deal
System and improvement.Chinese patent CN103276307A disclose a kind of highly corrosion resistant high ductility high chromium ferritic stainless steel steel plate and
Its manufacture method, i.e., by adding appropriate Ni and V, and improve high chromium Fe-Cr-Mo systems ferrite by control process
The low-temperature impact toughness of stainless-steel sheet, finally promote the brittle transition temperature of high chromium Fe-Cr-Mo systems ferritic stainless steel-
Less than 40 DEG C.But the steel plate thickness of the high chromium Fe-Cr-Mo systems ferritic stainless steel of foregoing invention be 0.5~5mm and from
The embodiment of above-mentioned patent can find its brittle transition temperature more than -80 DEG C, fail to promote the fragility of ferritic stainless steel
Transition temperature is down to extremely low（Less than -100 DEG C）.Meanwhile this patent and Cu is not added with, Mn, Nb and Ti content are high, and Al content is low,
And fail to be controlled and improve for the brittle transition temperature of Fe-Cr systems ferritic stainless steel cut deal.
Chinese patent CN102162063A discloses a kind of ferritic stainless steel cut deal and its manufacture method, i.e., by adding
Add 0.05~0.1% rare earth element to obtain the chromium content with compared with high-tensile, preferably anti-lamellar tearing performance be 11.5
~13.5% ferritic stainless steel cut deal.Wherein, rare earth element is the one or more in cerium, dysprosium, neodymium and yttrium.On however,
State patent and be not directed to the ferritic stainless steel cut deal that ferritic stainless steel, especially chromium content are more than 18%, Transition of Brittleness
Temperature still need reduce this shortcoming be controlled and improve.Chinese patent CN101733274A discloses a kind of high ferrochrome in improving
The hot-rolling method of ferritic stainless steel combination property, i.e., improve the formability of ferrite stainless steel sheet using final rolling temperature is reduced
Energy and surface quality.But above-mentioned patent is not directed to ferrite stainless steel mechanical property, especially thickness is more than 5mm's
The brittle transition temperature of ferritic stainless steel cut deal is controlled and improved.
Analyzed by above-mentioned patent, still needed for brittle transition temperature of the middle chromium without molybdenum ferritic stainless steel and improve this
The prior art of one deficiency and shortcoming is less, and middle chromium of the prior art can't fully meet mesh without molybdenum ferritic stainless steel
Preceding manufacture and requirement, still suffer from brittle transition temperature height and allow to use small some shortcoming and defect of grade of maximum gauge, need
A kind of middle chromium of extremely low brittle transition temperature is developed without molybdenum ferritic stainless steel cut deal.
The content of the invention
There is provided for existing ferritic stainless steel cut deal in above mentioned problem present on technology of preparing and performance, the present invention
A kind of middle chromium of extremely low brittle transition temperature without molybdenum ferritic stainless steel and preparation method thereof, by composition design and smelt and after
The improvement of continuous handling process, significantly reduces brittle transition temperature of the middle chromium without molybdenum ferritic stainless steel cut deal, improves ferrite
Service life and security of the stainless steel under the harsh Service Environment such as low temperature.
Composition of the middle chromium of extremely low brittle transition temperature without molybdenum ferritic stainless steel of the present invention contains C by mass percentage
0.005~0.015%, N 0.005~0.015%, Si≤0.5%, Mn≤0.2%, P≤0.03%, S≤0.01%, O≤0.005%,
Cr 18~22%, Nb 0.08~0.18%, Ti 0.05~0.1%, Ni 0.2~0.4%, Al 0.1~0.2%, Cu 0.3~
0.5%, surplus is iron and inevitable impurity, and 5.5~8mm of thickness, brittle transition temperature is at -120~-100 DEG C.
Preparation method of the middle chromium of extremely low brittle transition temperature without molybdenum ferritic stainless steel of the present invention is entered according to the following steps
OK：
（1）Smelt：Smelted by above-mentioned set component in vacuum induction melting furnace, and pour into strand；
（2）Hot rolling：By heating strand to 1000~1200 DEG C, 60~150min is incubated, then multistage hot deformation, open rolling temperature
To spend for 950~1100 DEG C, draught per pass is 30~50%, 650~750 DEG C of finishing temperature, accumulation drafts is 96~
98%, obtain hot rolled plate；
（3）Annealing：Hot rolled plate is heated to 850~950 DEG C, 6~8min is incubated, it is fully recrystallized to complete hot rolling
Annealing, chromium is without molybdenum ferritic stainless steel in acquisition.
The inventive method has the following advantages and effect compared with original technology：
1st, the brittle transition temperature of cut deal of the middle chromium without molybdenum ferritic stainless steel prepared significantly drops below -100 DEG C
Low brittle transition temperature of the middle chromium without molybdenum ferritic stainless steel cut deal, improves it under the harsh Service Environment such as low temperature
Service life and security, so as to reduce its life cycle cost to a certain extent；
2nd, cut deal of the middle chromium without molybdenum ferritic stainless steel, which is applied to make requirement, withstands shocks load and high impact toughness
Structure member, expand nickel-saving type ferritic stainless steel as the application of structural material and using thickness；Meanwhile also may be used
Make nickel-saving type ferritic stainless steel the parts such as building decoration, desalinization, power plant, petrochemical industry are civilian and industrial circle in further
Instead of the high chromiumnickel austenite stainless steel of price, the roof, curtain wall and various decorations for being such as used for coastal building are used
Material, the relevant device of seawater desalting plant, the equipment in the cooling system of power plant, the production of organic acid plant and storage and transport are set
Standby and pipeline, the heat exchanger etc. in chemical plant；This will can be not only that country saves a large amount of mineral resources（Such as nickel resources）, and
The production cost of steel will be also substantially reduced, finally realizes that stainless steel production economizes on resources, energy-saving and emission-reduction and prevented the pollution of the environment
Target, promote the sustainable development of stainless steel industry.
Brief description of the drawings
Fig. 1 is the brittle transition temperature of common middle chrome ferritic stainless steel 439 with the change curve of steel plate thickness；
Fig. 2 is micro-organization chart of the middle chromium without molybdenum ferritic stainless steel in the embodiment of the present invention 1；
Fig. 3 is impact absorbing energy-temperature profile of the middle chromium without molybdenum ferritic stainless steel in the embodiment of the present invention 1；
Fig. 4 is impact absorbing energy-temperature profile of the middle chromium without molybdenum ferritic stainless steel in the embodiment of the present invention 2；
Fig. 5 is impact absorbing energy-temperature profile of the middle chromium without molybdenum ferritic stainless steel in the embodiment of the present invention 3；
Fig. 6 is common middle micro-organization chart of the chromium without molybdenum ferritic stainless steel in comparative example 1；
Fig. 7 is common middle impact absorbing energy-temperature profile of the chromium without molybdenum ferritic stainless steel in comparative example 1；
Fig. 8 is common middle micro-organization chart of the chromium without molybdenum ferritic stainless steel in comparative example 2；
Fig. 9 is common middle micro-organization chart of the chromium without molybdenum ferritic stainless steel in comparative example 3.
Embodiment
The smelting of strand is completed in ZG-0.05 vacuum induction melting furnaces in the embodiment of the present invention and comparative example, work
When vacuum in 0.1~10Pa.
The hot rolling of strand is to test hot-rolling mill in Φ 450mm × 450mm two-roller reversibles in the embodiment of the present invention and comparative example
Upper progress.
The hot-roll annealing of rolled plate is in the multi-functional through heat of RX-36-10 types in the embodiment of the present invention and comparative example
Carried out in treatment furnace.
The Charpy-type test of ferritic stainless steel and the measurement of brittle transition temperature in the embodiment of the present invention and comparative example
It is according to GB/T229-2007, is carried out using Instron9250HV types shock machine and liquid nitrogen cryogenics groove.
The tensile test at room temperature of ferritic stainless steel and the measurement of mechanical property are according to GB/ in the embodiment of the present invention
T228.1-2010, carried out using Instron universal testing machines.
Yield strength of the middle chromium of extremely low brittle transition temperature without molybdenum ferritic stainless steel of the embodiment of the present invention be 250~
265MPa, tensile strength are 425~450MPa, and elongation percentage is 33~36%.
The embodiment of the present invention is described in further detail below, but embodiments of the present invention are not limited to
This.
Embodiment 1
Smelted by set component in vacuum induction melting furnace, and pour into strand；Strand composition contains C by mass percentage
0.005%, N 0.015%, Si 0%, Mn 0%, P 0.03%, S 0.007%, O 0.005%, Cr 18%, Nb 0.18%, Ti
0.05%, Ni 0.4%, Al 0.2%, Cu 0.3%, surplus are iron and inevitable impurity；
By heating strand to 1000 DEG C, 150min being incubated, then multistage hot deformation, start rolling temperature is 950 DEG C, every time
Drafts is 30~50%, 650 DEG C of finishing temperature, and accumulation drafts is 96%, obtains hot rolled plate；
Hot rolled plate is heated to 850 DEG C, 8min is incubated, it is fully recrystallized to complete hot-roll annealing, in acquisition chromium without
Molybdenum ferritic stainless steel, thickness 8mm, microscopic structure are as shown in Figure 2.After Charpy-type test, chromium is obtained in this without molybdenum-iron
Impact absorbing energy-temperature curve of ferritic stainless steel, as shown in figure 3, its brittle transition temperature is -100 DEG C.Tried through room temperature tensile
After testing, mechanical property of the chromium without molybdenum ferritic stainless steel in this is obtained, its yield strength is 250MPa, and tensile strength is
450MPa, elongation percentage 36%.
Embodiment 2
Smelted by set component in vacuum induction melting furnace, and pour into strand；Strand composition contains C by mass percentage
0.009%, N 0.011%, Si 0.3%, Mn 0.1%, P 0.02%, S 0.005%, O 0.003%, Cr 20%, Nb 0.13%, Ti
0.08%, Ni 0.3%, Al 0.18%, Cu 0.4%, surplus are iron and inevitable impurity；
By heating strand to 1100 DEG C, 90min being incubated, then multistage hot deformation, start rolling temperature is 1050 DEG C, every time
Drafts is 30~50%, 700 DEG C of finishing temperature, and accumulation drafts is 97%, obtains hot rolled plate；
Hot rolled plate is heated to 900 DEG C, 7min is incubated, it is fully recrystallized to complete hot-roll annealing, in acquisition chromium without
Molybdenum ferritic stainless steel, thickness 6mm, impact absorbing energy-temperature curve is as shown in figure 4, brittle transition temperature at -115 DEG C, is bent
It is 265MPa to take intensity, tensile strength 425MPa, elongation percentage 33%.
Embodiment 3
Smelted by set component in vacuum induction melting furnace, and pour into strand；Strand composition contains C by mass percentage
0.015%, N 0.005%, Si 0.5%, Mn 0.2%, P 0.01%, S 0.006%, O 0.002%, Cr 22%, Nb 0.08%, Ti
0.1%, Ni 0.2%, Al 0.1%, Cu 0.5%, surplus are iron and inevitable impurity；
By heating strand to 1200 DEG C, 60min being incubated, then multistage hot deformation, start rolling temperature is 1100 DEG C, every time
Drafts is 30~50%, 750 DEG C of finishing temperature, and accumulation drafts is 98%, obtains hot rolled plate；
Hot rolled plate is heated to 950 DEG C, 6min is incubated, it is fully recrystallized to complete hot-roll annealing, in acquisition chromium without
Molybdenum ferritic stainless steel, thickness 5.5mm, impact absorbing energy-temperature curve as shown in figure 5, brittle transition temperature at -120 DEG C,
Yield strength is 260MPa, tensile strength 440MPa, elongation percentage 34%.
Comparative example 1
With embodiment 1, difference is method：The content of Ni, Al and Cu in strand composition are 0, and other parts are pressed
Ferritic stainless steel is made in same way, its microscopic structure such as Fig. 6, and its impact absorbing energy-temperature curve is as shown in fig. 7, fragility
Transition temperature is 0 DEG C.
Comparative example 2
With embodiment 2, difference is method；The content of Al and Cu in strand composition are 0, and other parts are by identical
Ferritic stainless steel is made in mode, and its microscopic structure is as shown in figure 8, brittle transition temperature is 5 DEG C.
Comparative example 3
With embodiment 2, difference is method：The content of Ni and Cu in strand composition are 0, and other parts press phase Tongfang
Ferritic stainless steel is made in formula, and its microscopic structure is as shown in figure 9, brittle transition temperature is 25 DEG C.
Comparative example 4
With embodiment 3, difference is method：The content of Ni and Al in strand composition are 0, and other parts press phase Tongfang
Ferritic stainless steel is made in formula, and its brittle transition temperature is 20 DEG C.
Comparative example 5
With embodiment 1, difference is method：The content of Ni, Al and Cu in strand composition are 0, and strand is in hot rolling
During finishing temperature be 800 DEG C, ferritic stainless steel is made in other parts in the same way, its brittle transition temperature be 10
℃。
Comparative example 6
With embodiment 2, difference is method：The content of Al and Cu in strand composition are 0, annealing process 1000
DEG C insulation 8min, ferritic stainless steel is made in other parts in the same way, and its brittle transition temperature is 25 DEG C.
Claims (1)
- A kind of 1. preparation method of the middle chromium of extremely low brittle transition temperature without molybdenum ferritic stainless steel, it is characterised in that described pole Composition of the middle chromium of low brittle transition temperature without molybdenum ferritic stainless steel contains C 0.005~0.015%, N by mass percentage 0.005~0.015%, Si≤0.5%, Mn≤0.2%, P≤0.03%, S≤0.01%, O≤0.005%, Cr 18~22%, Nb 0.08~0.18%, Ti 0.05~0.1%, Ni 0.2~0.4%, Al 0.1~0.2%, Cu 0.3~0.5%, surplus is for iron and not Evitable impurity, 5.5~8mm of thickness, brittle transition temperature is at -120~-100 DEG C；Method is carried out according to the following steps：（1）Smelt：Smelted by above-mentioned set component in vacuum induction melting furnace, and pour into strand；（2）Hot rolling：By heating strand to 1000~1200 DEG C, 60~150min is incubated, then multistage hot deformation, start rolling temperature are 950~1100 DEG C, draught per pass is 30~50%, 650~750 DEG C of finishing temperature, and accumulation drafts is 96~98%, is obtained Obtain hot rolled plate；（3）Annealing：Hot rolled plate is heated to 850~950 DEG C, 6~8min is incubated, it is fully recrystallized and moved back with completing hot rolling Fire, chromium is without molybdenum ferritic stainless steel in acquisition.
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