CN108467991A - A kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature - Google Patents
A kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature Download PDFInfo
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- CN108467991A CN108467991A CN201810200764.3A CN201810200764A CN108467991A CN 108467991 A CN108467991 A CN 108467991A CN 201810200764 A CN201810200764 A CN 201810200764A CN 108467991 A CN108467991 A CN 108467991A
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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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- 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
- C21D8/0236—Cold rolling
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C21D2211/001—Austenite
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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
- C21D2211/004—Dispersions; Precipitations
Abstract
The present invention provides a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：C：0.3‑0.6%；Si：0.02‑0.1%；Mn：20.0‑26.0%；Al：0.5‑2.5%；Nb：0.05‑0.3%；P：≤0.010%；S：≤0.002%；N：0.004‑0.010%；O：0.0005‑0.002%；Surplus is Fe.The present invention furthermore provides a kind of heat treatment process of the high-strength high-ductility high manganese steel for ultralow temperature.A kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature provided by the invention, pass through the heat treatment process of cold rolling+low temperature aging+high temperature re-crystallization, prepare the high-strength high-ductility high manganese steel for ultralow temperature, with good intensity and excellent plasticity, and it is with good weldability, cost is relatively low, and heat treatment process is more simple.
Description
Technical field
The invention belongs to the technical field of cryogenic steel, it is related at a kind of high-strength high-ductility high manganese steel for ultralow temperature and its heat
Science and engineering skill.
Background technology
It is high-strength with the fast development of the equipment manufacturings such as global ocean drilling platforms, sea-bottom oil-gas conveying and Oil ＆ Gas Storage
The demand of high tenacity cryogenic steel, the low temperature sea work steel especially used under marine environment significantly rises.Currently, extensively
Steel material applied to ultralow temperature is mainly richness Ni ferrite types low-temperature steel and Austenitic low-temperature steel.With offshore platform steel
For, high strength steel accounts for 55-60% in self-elevating drilling platform, account for 90-98% in semisubmersible drilling platform, wherein platform
Spud leg, cantilever beam and upgrading rackwork etc. require to take into account excellent low temperature while proof strength rank (460-690MPa)
Impact flexibility (- 80 DEG C of ballistic works>100J).
Ni systems ferritic steel for low temperature service and austenitic stainless steel are although functional, but expensive, and Ni elements are to low
The low-temperature flexibility influence of Wen Gang is very big, and content is higher, and influence is bigger.Therefore, high manganese systems Austenitic low-temperature steel be developing progressively for
The most low temperature structure material of practicability and economy, although Mn is highly effective for reducing Ductile-brittle transition temperature
, by improving the Mn/C ratios in low-temperature steel, it is remarkably improved the toughness of steel.But the surrender pole of single phase austenite type low-temperature steel
It limits relatively low, is unable to reach ideal strength level, comprehensive obdurability is poor.Therefore, it is necessary to the tough of high manganese systems low-temperature steel
Change further research and discussion.
To ensure that high manganese systems low-temperature steel has excellent intensity, a variety of strengthening mechanisms need to be introduced, such as refined crystalline strengthening and precipitation
Strengthen；In order to make precipitation strength not destroy the plasticity of low-temperature steel, then precipitate size need to be Nano grade, using addition Al,
The elements such as Nb form various types of nano silicon carbide composition granules such as κ carbide and MC type carbide.Meanwhile in the base of crystal grain refinement
It needs to can guarantee that austenite remains to generate twin crystal induction plastic (TWIP) effect under low-temperature deformation on plinth, generally by controlling Ovshinsky
The constituent content and crystallite dimension in internal portion, could control its stacking fault energy (SFE) and deformation mechanism.It is difficult to understand such as when Mn too high levels
Family name's body stacking fault energy is very high, and low-temperature deformation mechanism is dislocation movement by slip, cannot generate twin；And when Mn contents are very low, Ovshinsky
Martensitic traoformation easily occurs under body hypothermia, it is crackle that interface, which is easy induction, therefore stacking fault energy needs stringent control.Meanwhile it is brilliant
Grain refinement can significantly inhibit the generation of twin, improve stability.Therefore, high manganese systems low-temperature steel is carried out by above-mentioned tissue need to close
Golden composition design, while proposing a kind of novel heat treatment process, prepare a kind of high manganese systems steel used at ultra-low temperature of high-strength tenacity.
Invention content
In view of the foregoing deficiencies of prior art, the purpose of the present invention is to provide a kind of height for ultralow temperature is tough
Potassium steel and its heat treatment process obtain effective crystal grain refinement using low temperature aging and high temperature re-crystallization processing and twin crystal are distributed
Austenite and nanometer precipitated phase complex tissue, for solving, existing manganese systems low temperature hardness of steel is relatively low and whole obdurability is poor
The problem of, and the structural steel for being used under ultra-low temperature surroundings can be manufactured.
In order to achieve the above objects and other related objects, it is tough to provide a kind of height for ultralow temperature for first aspect present invention
Potassium steel is made of the element of following mass percent：
C (carbon)：0.3-0.6%；Si (silicon)：0.02-0.1%；Mn (manganese)：20.0-26.0%；Al (aluminium)：0.5-
2.5%；Nb (niobium)：0.05-0.3%；P (phosphorus)：≤ 0.010%；S (sulphur)：≤ 0.002%；N (nitrogen)：0.004-0.010%；O
(oxygen)：0.0005-0.002%；Surplus is Fe (iron).
Preferably, a kind of high-strength high-ductility high manganese steel for ultralow temperature, element composition optionally following one：
1) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.3-0.4%；Si：0.02-0.05%；Mn：25.0-26.0%；Al：1.5-2.5%；Nb：0.06-0.3%；
P：≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
2) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.4-0.5%；Si：0.02-0.1%；Mn：23.0-25.0%；Al：0.5-2.5%；Nb：0.06-0.25%；
P：≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
3) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.4-0.6%；Si：0.05-0.1%；Mn：22.5-24.0%；Al：0.5-1.5%；Nb：0.06-0.25%；
P：≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
It is highly preferred that a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.4-0.5%；Si：0.02-0.05%；Mn：23.5-24.5%；Al：1.5-2.5%；Nb：0.06-
0.15%；P：≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
The element composition of high-strength high-ductility high manganese steel in the present invention, wherein carbon can significantly improve the intensity of low-temperature steel and carry
The stability of high austenite, and be effective carbide former.Manganese element can effectively reduce ductile brittle transition temperature
Degree is remarkably improved the toughness of steel by improving the Mn/C ratios in low-temperature steel.In addition, suitable aluminium etc. is added in low-temperature steel
Element can effectively improve the stacking fault energy of austenite, and form the nano particle of similar κ carbide, while add micro Nb members
Element can form the MC carbide of rich niobium, ensure its low-temperature flexibility while can increasing substantially intensity.Meanwhile for manganese systems low temperature
Steel most importantly controls the content of the impurity elements such as S, P, N and O in smelting process, inhibits the formation of field trash such as MnS,
This is the important means for improving low-temperature steel low-temperature flexibility.
Second aspect of the present invention provides a kind of heat treatment process of the high-strength high-ductility high manganese steel for ultralow temperature, including following step
Suddenly：
A steel ingot is cast after) taking each element component to mix according to the ratio, steel ingot is heated and kept the temperature at 1150-1250 DEG C
After >=2h, then carried out by 1045-1055 DEG C of breaking down temperature to 745-755 DEG C of finishing temperature air-cooled after multistep hot rolling；
B the steel ingot after) will be air-cooled is heat-treated, and obtains cold-reduced sheet after first carrying out cold-rolling treatment, then cold-reduced sheet is existed
450-550 DEG C of temperature range carries out after 2-4h is precipitated in low temperature aging water quenching to room temperature, finally carries out after high temperature re-crystallization water again
It quenches to room temperature to get in the high-strength high-ductility high manganese steel of ultralow temperature.
Preferably, step A) in, the temperature of the heating is 1200 DEG C.
Preferably, step A) in, the breaking down temperature is 1050 DEG C, and the finishing temperature is 750 DEG C.
Preferably, step A) in, the multistep hot rolling includes the following steps：
The first step：Hot-rolled temperature：1045-1055 DEG C, soaking time：165-175 minutes；
Second step：Hot-rolled temperature：975-985 DEG C, soaking time：115-125 minutes；
Third walks：Hot-rolled temperature：845-855 DEG C, soaking time：85-95 minutes；
4th step：Hot-rolled temperature：825-835 DEG C, soaking time：65-75 minutes；
5th step：Hot-rolled temperature：805-815 DEG C, soaking time：45-55 minutes；
6th step：Hot-rolled temperature：775-785 DEG C, soaking time：35-45 minutes；
7th step：Hot-rolled temperature：765-775 DEG C, soaking time：27-37 minutes；
8th step：Finishing temperature：745-755 DEG C, soaking time：20-30 minutes.
It is highly preferred that the multistep hot rolling includes the following steps：
The first step：Hot-rolled temperature：1050 DEG C, soaking time：170 minutes；
Second step：Hot-rolled temperature：980 DEG C, soaking time：120 minutes；
Third walks：Hot-rolled temperature：850 DEG C, soaking time：90 minutes；
4th step：Hot-rolled temperature：830 DEG C, soaking time：70 minutes；
5th step：Hot-rolled temperature：810 DEG C, soaking time：50 minutes；
6th step：Hot-rolled temperature：780 DEG C, soaking time：40 minutes；
7th step：Hot-rolled temperature：770 DEG C, soaking time：32 minutes；
8th step：Finishing temperature：750 DEG C, soaking time：25 minutes.
Preferably, step A) in, each reduction ratio of the multistep hot rolling is maintained at 20-30%.
The reduction ratio common reduction ratio expression deformation extent for indicating relative deformation when referring to rolling and forging and stamping.Work as multistep
When rolling reduction ratio is maintained as possible in a stability range, effect of rolling is preferable.
Preferably, step B) in, the process of the heat treatment includes cold-rolling treatment, low temperature aging, high temperature re-crystallization.
Preferably, step B) in, the cold-rolling treatment carries out single step rolling at room temperature.
It is highly preferred that the reduction ratio of the cold-rolling treatment is 60-75%.
Preferably, step B) in, the temperature range of the low temperature aging is 480-530 DEG C, the precipitation of the low temperature aging
Time is 3-4h.It is highly preferred that the temperature of the low temperature aging is 500 DEG C, the precipitation time of the low temperature aging is 3h.
Preferably, step B) in, the temperature range of the high temperature re-crystallization is 750-850 DEG C, the high temperature re-crystallization
Soaking time is 60-90s.
It is highly preferred that the temperature range of the high temperature re-crystallization is 780-830 DEG C, the soaking time of the high temperature re-crystallization
For 70-90s.
It is further preferred that the temperature range of the high temperature re-crystallization is 800 DEG C, the soaking time of the high temperature re-crystallization
For 90s.
Preferably, step B) in, the water quenching is to be water-cooled to the product after low temperature aging or high temperature re-crystallization
Room temperature.
Above-mentioned room temperature is 20-25 DEG C.
As described above, a kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature provided by the invention, passes through
Cold rolling+low temperature aging+high temperature re-crystallization technique, chooses suitable aging temp and time, and the first step is realized effectively in matrix
Nanometer phase disperse educt, the very high dislocation density of matrix can promote the precipitation of carbide, and second step recrystallization process is by receiving
The pinning effect of rice precipitated phase obtains the complex tissue of the austenite and precipitated phase of size gradient distribution, passes through nanometer precipitated phase
With twin crystal distribution austenite combined influence, during cryogenic tensile utilize austenite TWIP effects, refined crystalline strengthening and
The precipitation strength of nanometer precipitated phase has good intensity and excellent plasticity, and it is with good weldability, cost compared with
Low, heat treatment process is more simple.
A kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature provided by the invention, it is low to solve existing manganese systems
The problem that warm hardness of steel is relatively low and whole obdurability is poor utilizes low temperature aging and high temperature re-crystallization processing to obtain effective brilliant
The complex tissue of the austenite and nanometer precipitated phase of grain refinement and twin crystal distribution, is effectively improved the obdurability of manganese systems low-temperature steel, energy
It is enough in the structural steel used under manufacture ultra-low temperature surroundings, can obtain and reach 900- in -196 DEG C of lower yield strengths
1100MPa, tensile strength reach 1400-1600MPa, elongation percentage reaches 50%-60% and impact flexibility reaches 100-130J/
cm2High-strength high-ductility high manganese steel.
Description of the drawings
Fig. 1 is shown as scanning electron microscope micro-organization chart 1a, 1b of the high-strength low temperature resistant steel of embodiment 1 in the present invention, wherein
1a is the scanning electron microscope micro-organization chart before heat treatment；1b is the scanning electron microscope micro-organization chart after heat treatment.
Fig. 2 is shown as scanning electron microscope micro-organization chart 2a, 2b of the high-strength low temperature resistant steel of embodiment 2 in the present invention, wherein
2a is the scanning electron microscope micro-organization chart before heat treatment；2b is the scanning electron microscope micro-organization chart after heat treatment.
Fig. 3 is shown as -196 DEG C of impact property figures before and after the high-strength low temperature resistant steel heat treatment of embodiment 1-2 in the present invention.
Specific implementation mode
With reference to specific embodiment, the present invention is further explained, it should be appreciated that these embodiments are merely to illustrate the present invention
Rather than it limits the scope of the invention.
Illustrate that embodiments of the present invention, those skilled in the art can be by this specification below by way of specific specific example
Disclosed content understands other advantages and effect of the present invention easily.The present invention can also pass through in addition different specific realities
The mode of applying is embodied or practiced, the various details in this specification can also be based on different viewpoints with application, without departing from
Various modifications or alterations are carried out under the spirit of the present invention.
It should be clear that in the following example not specifically dated process equipment or device be all made of conventional equipment in the art or
Device；All pressure values and range all refer to relative pressure.
In addition, it should also be understood that, one or more method and step mentioned in the present invention does not repel before and after the combination step
It can also be inserted into other methods step there may also be other methods step or between these explicitly mentioned steps, unless separately
It is described；It should also be understood that the combination connection relation between one or more equipment/device mentioned in the present invention is not repelled
The front and back two equipment/devices specifically mentioned there may also be other equipment/device or at these of the unit equipment/device it
Between can also be inserted into other equipment/device, unless otherwise indicated.Moreover, unless otherwise indicated, the number of various method steps is only
Differentiate the convenient tool of various method steps, rather than to limit the ordering of various method steps or limiting the enforceable model of the present invention
It encloses, relativeness is altered or modified, and without material changes in technical content, when being also considered as, the present invention is enforceable
Scope.
The raw material of the elements such as carbon containing, silicon, manganese, aluminium, niobium, phosphorus, sulphur, nitrogen, oxygen, iron that following embodiment uses can be from market
Upper purchase realizes that the equipment of the techniques such as hot rolling treatment, cold-rolling treatment, low temperature aging, high temperature re-crystallization, water quenching also can be from the market
Purchase obtains.
Embodiment 1
Cast steel ingot after taking the raw material of the component containing each element to mix according to the ratio, each component by following mass percent element
Composition：C：0.4-0.5%；Si：0.02-0.1%；Mn：23.0-25.0%；Al：0.5-2.5%；Nb：0.06-0.25%；P：
≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.By steel ingot 1200
After DEG C being heated and keep the temperature 2h, then air-cooled, steel ingot after multistep hot rollings carried out by 1050 DEG C of breaking down temperature to 750 DEG C of finishing temperature
Thickness is 240mm.Wherein, multistep hot-rolled condition is：Respectively continuously at 1050,980,850,830,810,780,770,750 DEG C
At a temperature of, reduction ratio is respectively 29.17%, 29.41%, 25%, 22.22%, 21.43%, 20%, 20%, 21.88%, is protected
The warm time is respectively 170,120,90,70,50,40,32,25 minutes.The derusting of potassium steel rolled steel plate is deoiled, cleaning is dry
Only, the unbalance stress phenomenon in heat treatment process is avoided.Ingot casting detects under a scanning electron microscope after will be hot rolled, specific aobvious
Micro-assembly robot figure is shown in Fig. 1 a.
Then, rolled processing low-temperature steel is subjected to cold rolling heat treatment, i.e. cold rolling reduction ratio is 70%, is then carried out low
Warm hardening carries out isothermal aging between i.e. 500 DEG C of temperature ranges and 3h, then water quenching to room temperature is precipitated；After low temperature aging is handled
Potassium steel carry out recrystallization 90s at 800 DEG C, finally carry out water quenching to room temperature.By the low temperature resistant high-strength high-ductility high manganese steel of acquisition
Sample 1# is detected under a scanning electron microscope, and Fig. 1 b see in specific micro-organization chart.
Embodiment 2
Cast steel ingot after taking the raw material of the component containing each element to mix according to the ratio, each component by following mass percent element
Composition：C：0.4-0.6%；Si：0.05-0.1%；Mn：22.5-24.0%；Al：0.5-1.5%；Nb：0.06-0.25%；P：
≤ 0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.By steel ingot 1200
After DEG C being heated and keep the temperature 2h, carried out by 1050 DEG C of breaking down temperature to 750 DEG C of finishing temperature air-cooled after multistep hot rollings, steel ingot is thick
Degree is 240mm.Wherein, multistep hot-rolled condition is：Respectively continuously in 1050,980,850,830,810,780,770,750 DEG C of temperature
Under degree, reduction ratio is respectively 29.17%, 29.41%, 25%, 22.22%, 21.43%, 20%, 20%, 21.88%, heat preservation
Time is respectively 170,120,90,70,50,40,32,25 minutes.The derusting of potassium steel rolled steel plate is deoiled, is cleaned up,
Avoid the unbalance stress phenomenon in heat treatment process.Ingot casting detects under a scanning electron microscope after will be hot rolled, specific micro-
Organization chart is shown in Fig. 2 a.
Then, rolled processing low-temperature steel is subjected to cold rolling heat treatment, i.e. cold rolling reduction ratio is 70%, is then carried out low
Warm hardening carries out isothermal aging between i.e. 500 DEG C of temperature ranges and 3h, then water quenching to room temperature is precipitated；After low temperature aging is handled
Potassium steel carry out recrystallization 90s at 800 DEG C, finally carry out water quenching to room temperature.By the low temperature resistant high-strength high-ductility high manganese steel of acquisition
Sample 2# is detected under a scanning electron microscope, and Fig. 2 b see in specific micro-organization chart.
Embodiment 3
Scanning electron microscope is respectively adopted in low temperature resistant high-strength high-ductility high manganese steel sample 1-2# in embodiment 1-2 to carry out
Austenite and precipitated phase observation, concrete outcome are shown in Fig. 1 a, 1b, 2a, 2b.
By Fig. 1 a, 1b, 2a, 2b it is found that the sample tissue crystal grain of rolled is very coarse, substantially at 12 μm or so, have big
Annealing twin circle of amount occurs.And after subsequent processing, crystallite dimension obviously attenuates, and is distributed in twin crystal, i.e., size is brilliant
Grain has, and Size Distribution is 0.4-5 μm.A large amount of non-uniform nanometer precipitated phases are dispersed in matrix simultaneously, size probably exists
Recrystallization after 5-20nm or so, substantially metaplasia caused by cold rolling are heat-treated is eliminated.The austenite of twin crystal distribution
Size have benefited from the precipitated phase generated in low temperature ageing process during recrystallization can pinning austenite grain boundary, inhibit
The growth process of austenite, and the distribution of non-uniform precipitated phase also results in different degrees of recrystallization.
Embodiment 4
Low temperature resistant high-strength high-ductility high manganese steel sample 1-2# in embodiment 1-2 is subjected to cryogenic tensile experiment respectively, specifically
It the results are shown in Table 1.As shown in Table 1, after Overheating Treatment, the yield strength and tensile strength of potassium steel are significantly improved to 900-
The rank of 1100MPa and 1400-1600MPa, and low temperature elongation percentage, according to up to 59% or more, the strength and ductility product under whole low temperature is warmmer
It is still improved before processing, this has benefited from the complex intensifying mechanism of refined crystalline strengthening and precipitation strength, while being generated in deformation process
Twin crystal induction plastic effect, while improving obdurability.
Low temperature resistant front and back -196 DEG C of tensile mechanical properties contrast tables of high-strength high-ductility high manganese steel heat treatment of table 1
Embodiment 5
It is real that low temperature resistant high-strength high-ductility high manganese steel sample product 1-2# in embodiment 1-2 is subjected to -196 DEG C of impacts of low temperature respectively
It tests, concrete outcome is shown in Fig. 3, table 1.By Fig. 3, table 1 it is found that high-strength high-ductility high manganese steel is after Overheating Treatment, rushing under liquid nitrogen temperature
Hitting toughness has certain decline, but impact flexibility remains above 100J/cm2.While keeping high intensity, still reach good
Low-temperature flexibility has been more than the impact flexibility standard value 42.5J/cm for potassium steel in ASTM standard2, obtain a kind of for surpassing
The high-strength high-ductility high manganese steel of low temperature.
In conclusion a kind of high-strength high-ductility high manganese steel and its heat treatment process for ultralow temperature provided by the invention, passes through
Cold rolling+low temperature aging+high temperature re-crystallization technique prepares the high-strength high-ductility high manganese steel for ultralow temperature, has good intensity
With excellent plasticity, and it with good weldability, cost is relatively low, and heat treatment process is more simple.So the present invention has
Effect overcomes various shortcoming in the prior art and has high industrial utilization.
The above-described embodiments merely illustrate the principles and effects of the present invention, and is not intended to limit the present invention.It is any ripe
The personage for knowing this technology can all carry out modifications and changes to above-described embodiment without violating the spirit and scope of the present invention.Cause
This, institute is complete without departing from the spirit and technical ideas disclosed in the present invention by those of ordinary skill in the art such as
At all equivalent modifications or change, should by the present invention claim be covered.
Claims (10)
1. a kind of high-strength high-ductility high manganese steel for ultralow temperature is made of the element of following mass percent：
C：0.3-0.6%；Si：0.02-0.1%；Mn：20.0-26.0%；Al：0.5-2.5%；Nb：0.05-0.3%；P：≤
0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
2. a kind of high-strength high-ductility high manganese steel for ultralow temperature according to claim 1, which is characterized in that element composition is optional
Following one：
1) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.3-0.4%；Si：0.02-0.05%；Mn：25.0-26.0%；Al：1.5-2.5%；Nb：0.06-0.3%；P：≤
0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe；
2) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.4-0.5%；Si：0.02-0.1%；Mn：23.0-25.0%；Al：0.5-2.5%；Nb：0.06-0.25%；P：≤
0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe；
3) a kind of high-strength high-ductility high manganese steel for ultralow temperature, is made of the element of following mass percent：
C：0.4-0.6%；Si：0.05-0.1%；Mn：22.5-24.0%；Al：0.5-1.5%；Nb：0.06-0.25%；P：≤
0.010%；S：≤ 0.002%；N：0.004-0.010%；O：0.0005-0.002%；Surplus is Fe.
3. according to a kind of heat treatment process of any high-strength high-ductility high manganese steels for ultralow temperature of claim 1-2, including
Following steps：
A steel ingot is cast after) taking each element component to mix according to the ratio, steel ingot is heated at 1150-1250 DEG C and keeps the temperature >=2h
Afterwards, then by 1045-1055 DEG C of breaking down temperature to 745-755 DEG C of finishing temperature it carries out air-cooled after multistep hot rolling；
B the steel ingot after) will be air-cooled is heat-treated, and obtains cold-reduced sheet after first carrying out cold-rolling treatment, then by cold-reduced sheet in 450-550
DEG C temperature range carries out after 2-4h is precipitated in low temperature aging water quenching to room temperature, finally carries out after high temperature re-crystallization water quenching again to room
Temperature is to get in the high-strength high-ductility high manganese steel of ultralow temperature.
4. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step
A in), the temperature of the heating is 1200 DEG C.
5. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step
A in), the breaking down temperature is 1050 DEG C, and the finishing temperature is 750 DEG C.
6. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step
A in), the multistep hot rolling includes the following steps：
The first step：Hot-rolled temperature：1045-1055 DEG C, soaking time：165-175 minutes；
Second step：Hot-rolled temperature：975-985 DEG C, soaking time：115-125 minutes；
Third walks：Hot-rolled temperature：845-855 DEG C, soaking time：85-95 minutes；
4th step：Hot-rolled temperature：825-835 DEG C, soaking time：65-75 minutes；
5th step：Hot-rolled temperature：805-815 DEG C, soaking time：45-55 minutes；
6th step：Hot-rolled temperature：775-785 DEG C, soaking time：35-45 minutes；
7th step：Hot-rolled temperature：765-775 DEG C, soaking time：27-37 minutes；
8th step：Finishing temperature：745-755 DEG C, soaking time：20-30 minutes.
7. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step B) in, the cold-rolling treatment carries out single step rolling at room temperature；The reduction ratio of the cold-rolling treatment is 60-75%.
8. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step B) in, the temperature range of the low temperature aging is 480-530 DEG C, and the precipitation time of the low temperature aging is 3-4h.
9. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, which is characterized in that
Step B) in, the temperature range of the high temperature re-crystallization is 750-850 DEG C, and the soaking time of the high temperature re-crystallization is 60-
90s。
10. a kind of heat treatment process of high-strength high-ductility high manganese steel for ultralow temperature according to claim 3, feature exist
In step B) in, the water quenching is to carry out the product after low temperature aging or high temperature re-crystallization to be water-cooled to room temperature.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113957353A (en) * | 2021-10-26 | 2022-01-21 | 东北大学 | High-manganese high-toughness steel applicable at 4.2K temperature and preparation method thereof |
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