CN107675077B - A kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof - Google Patents
A kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof Download PDFInfo
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- 229910001563 bainite Inorganic materials 0.000 title claims abstract description 65
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 46
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 38
- 238000002360 preparation method Methods 0.000 title claims abstract description 32
- 229910000754 Wrought iron Inorganic materials 0.000 title abstract description 24
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 21
- 239000000126 substance Substances 0.000 claims abstract description 18
- 238000005096 rolling process Methods 0.000 claims abstract description 15
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910000831 Steel Inorganic materials 0.000 claims description 42
- 239000010959 steel Substances 0.000 claims description 42
- 238000005098 hot rolling Methods 0.000 claims description 22
- 238000000137 annealing Methods 0.000 claims description 19
- 150000003839 salts Chemical class 0.000 claims description 19
- 238000001816 cooling Methods 0.000 claims description 10
- 238000010583 slow cooling Methods 0.000 claims description 8
- 238000000265 homogenisation Methods 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 claims 4
- 238000004519 manufacturing process Methods 0.000 abstract description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 7
- 238000003466 welding Methods 0.000 abstract description 5
- 239000007769 metal material Substances 0.000 abstract description 4
- 230000007704 transition Effects 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 abstract description 3
- 230000001744 histochemical effect Effects 0.000 abstract 1
- 230000009466 transformation Effects 0.000 description 23
- 238000004321 preservation Methods 0.000 description 15
- 239000011572 manganese Substances 0.000 description 13
- 229910000734 martensite Inorganic materials 0.000 description 13
- 238000000034 method Methods 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 238000005266 casting Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 229910000859 α-Fe Inorganic materials 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000005275 alloying Methods 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 239000002086 nanomaterial Substances 0.000 description 4
- 230000000717 retained effect Effects 0.000 description 4
- 230000005540 biological transmission Effects 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 238000010891 electric arc Methods 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- 208000015943 Coeliac disease Diseases 0.000 description 2
- 229910000677 High-carbon steel Inorganic materials 0.000 description 2
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 235000013339 cereals Nutrition 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 206010054949 Metaplasia Diseases 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 229910006638 Si—Mn—Al Inorganic materials 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 235000021050 feed intake Nutrition 0.000 description 1
- 235000000396 iron Nutrition 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000015689 metaplastic ossification Effects 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 238000003359 percent control normalization Methods 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 235000015170 shellfish Nutrition 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
-
- 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
-
- 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
- C21D2211/002—Bainite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention provides a kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof, belong to metal material field, technical solution is a kind of middle carbon nanometer bainite unimach, and chemical quality percentage is as follows: C:0.52 ~ 0.58%, Si:1.5 ~ 1.8%, Mn:1.6 ~ 2.0%, Mo:0.18 ~ 0.24%, Ni:1.2 ~ 1.7%, P: < 0.02%, S: < 0.02%, surplus is Fe and inevitable impurity.The utility model has the advantages that unimach and rod iron histochemical components scientific matching of the invention, the accurate preparation method of cooperation science, strengthen with overcooling austenite rolling deformation, so that nanometer bainite structure starts transition temperature and transition temperature and reduces, crystal grain refinement, dislocation retains, intensity is high, plasticity is good, good welding performance, and production efficiency improves, it is at low cost.
Description
Technical field
The present invention relates to metal material fields, and in particular to a kind of middle carbon nanometer bainite unimach, rod iron and its
Preparation method.
Background technique
Nanometer bainite structure of steel has high-intensitive, higher fracture toughness and preferable compression plasticity, comprehensive performance excellent
Good, United States Patent (USP) US6884306 has invented a kind of Si-Mn-Cr-Ni-Mo-V nanometers of bainitic steel, C and Si content is higher in steel,
Respectively reach 0.6 ~ 1.1% and not less than 1.5%(weight percent), the prolonged homogenizing annealing of first high temperature after ingot casting slow cooling,
Overcooling austenite Isothermal Bainite is carried out in the low temperature of a little higher than steel Ms (martensite start) point after austenitizing again to turn
Become, obtains the nanometer bainite structure being made of the lath bainitic ferrite and retained austenite of nanometer grade thickness, but the party
Method fringe time is up to 1 ~ 3 week, low efficiency, long preparation period.
In order to accelerate Isothermal Bainite to change, shortens the production cycle, add in above-mentioned high-carbon Si-Mn-Cr-Ni-Mo-V steel
Add Co or Co+Al, the bainite transformation time can be made to greatly shorten, but Co price is high, cost of alloy greatly increases.Chinese invention is special
Sharp CN101693981A discloses a kind of preparation method of low-alloy high-carbon steel with high-strength and high ductility nano structure, i.e., in high-carbon steel
It adds Mn, Cr, Si, Al, W and carries out alloying, not adding Co reduces cost, and ingot casting carries out being rolled into slab and eliminates casting and lack
It falling into, hot rolling slab isothermal bainite transformation directly in salt bath has obtained nanometer bainite structure, and tensile strength is 2000 ~
2300MPa, breaking elongation are 6.7 ~ 7.8%.But the weldability and impact flexibility of this high-carbon nanometer bainitic steel are poor, significantly
Limit its application range as structural steel.In order to extend the application range of this nanometer bainite structure, researcher's examination
Figure in carbon content is lower, in low carbon and high silicon steel prepare nanometer bainite, but carbon content reduce, so that martensite transfor mation is started temperature
Degree increases, this temperature that Isothermal Bainite is changed improves, and degree of supercooling reduces, and lath of bainite thickness will increase, unfavorable
In obtaining nanometer bainite, further researcher inhibits to draw since carbon content reduces by adding more alloying element Ni
The Ms (martensite start) point risen increases, but which results in the gap mistakes between martensite and bainite start temperature
It is small, so that the temperature window of bainite transformation is almost disappeared, is also unfavorable for obtaining nanometer bainite structure.Applicant is in middle promulgated by the State Council
A kind of preparation side of nanostructure carbide-free bainite medium-carbon alloy steel is disclosed in bright patent ZL 201110255203.1
Method, this method deform to reduce Ms (martensite start) point and improve austenite intensity using overcooling austenite cold plasticity,
To allow deformed austenite in lower temperature isothermal transformation, austenite intensity raising in addition increases its shear drag, causes
The lath of bainite thickness for obtaining isothermal transformation significantly reduces, and a nanometer bainite structure is so obtained in medium carbon steel.
But in the chemical component for being suitable for preparing nanometer bainitic steel of the patent disclosure, containing a large amount of alloying element, cost of alloy is too
Height, moreover, the preparation of this nanometer bainitic steel is completed on thermomechanical simulation test machine, prepared nanometer bainite
Steel curved beam size is too small, using being also extremely restricted.The Chinese invention patent of application number 03150091.9, disclose with C,
Mn, Si be main alloy element middle carbon and medium high carbon manganese systems air-cooled bainitic steels, it is air-cooled tissue be carbide-free Bainite and
The heterogeneous structure of martensite, the tensile strength after lonneal are 1900MPa, elongation percentage 7%, and intensity is far below high-carbon nanometer
Bainitic steel, and the martensite in this heterogeneous structure can reduce plasticity and toughness.Application No. is 201610461170.9 middle promulgateds by the State Council
Bright patent discloses the high strength and ductility nanostructure bainitic steel for body of a motor car anticollision component, C content percentage by weight
Than being 0.55 ~ 0.65, belong to medium carbon steel, preparation step is related to three step isothermal transformation, accumulate total isothermal transformation time up to 34 ~
120h, and the tensile strength of prepared nanostructure bainitic steel is only 1421 ~ 1771MPa, elongation percentage is 10.7 ~
11.4%, the production cycle is long, and product strength is far below high-carbon nanometer bainitic steel.The China of application number 201310423172.5
Patent of invention discloses a kind of 2100MPa nanometers of bainitic steel and preparation method thereof, which contains a large amount of Co and Al, at high cost
And there are continuous casting sprues to block risk, tensile strength is up to 2070MPa in the embodiment provided, and elongation percentage only has 6%, and waits
Warm fringe time is up to 96h.The Chinese invention patent of application number 201410135887.5, disclose a kind of 2400MPa grades it is low
The preparation method of cost nanometer bainitic steel, the steel are C-Si-Mn-Al system, and chemical component is by weight percentage are as follows: C 0.50 ~
1.00, Si 2.00 ~ 3.00, Mn 0.30 ~ 0.50, Al 0.50 ~ 1.00, isothermal transformation obtain a nanometer bainite structure, embodiment
In as it can be seen that the carbon content of steel is respectively 0.6,0.8 and 0.9 by weight percentage, tensile strength and prolong after 230 DEG C of isothermal transformation
The rate of stretching is respectively 2390MPa, 2399MPa, 2339MPa and 7.0%, 3.1%, 1.3%；And the tensile strength after 300 DEG C of isothermal transformation
1803MPa, 1975MPa, 1955MPa and 11.3%, 12.5%, 15.6% are distinguished with elongation percentage.The nanometer bainite of this method preparation
Elongation percentage is lower when hardness of steel is close to 2400MPa, and wherein to easily lead to continuous casting sprue during the preparation process stifled by the higher Al of content
Plug, the high Si of content easily cause brittleness to increase and be unfavorable for welding.In summary it finds, at present carbon nanometer bainitic steel in acquisition
The method of tissue, there are many difficult points, such as the production cycle is long, at high cost, plasticity is poor, brittleness is big, and obtained structure of steel is comprehensive
Performance is bad, and application is significantly limited.
Summary of the invention
To solve, the existing middle carbon nanometer bainite structure of steel production cycle is long, at high cost, plasticity is poor, brittleness is big, comprehensive
Can difference technical problem, the present invention provides a kind of middle carbon nanometer bainite unimach, rod iron and preparation method thereof, passes through section
Accurate optimization structure of steel chemical constituent is learned, the accurate ingot casting that controls carries out consumable, homogenizing annealing and hot rolling, further spheroidizing
Afterwards, then heat preservation and salt bath cooling are reheated, is strengthened using overcooling austenite rolling deformation, reduced martensite and start transformation temperature
Degree, and accelerate bainite transformation, it shortens the production cycle to realize, reduce alloying element cost, obtained middle carbon is received
Rice bainite superhigh intensity rod iron quality stability height, intensity and hardness greatly improve, plasticity is good.
The technical solution adopted by the present invention is that:
A kind of middle carbon nanometer bainite unimach, chemical quality percentage are as follows:
C:0.52 ~ 0.58%, Si:1.5 ~ 1.8%, Mn:1.6 ~ 2.0%, Mo:0.18 ~ 0.24%, Ni:1.2 ~ 1.7%, P: <
0.02%, S: < 0.02%, surplus is Fe and inevitable impurity.
The present invention also provides a kind of middle carbon nanometer bainite superhigh intensity rod irons, and the rod iron chemical quality percentage is such as
Under: C:0.52 ~ 0.58%, Si:1.5 ~ 1.8%, Mn:1.6 ~ 2.0%, Mo:0.18 ~ 0.24%, Ni:1.2 ~ 1.7%, P: < 0.02%, S:
< 0.02%, surplus is Fe and inevitable impurity, and tensile strength is not less than 2200 MPa, hardness is not less than 606HV1.0, total
Elongation percentage is not less than 8.5%.
The present invention also provides a kind of preparation method of middle carbon nanometer bainite superhigh intensity rod iron, the chemical matter of the rod iron
It is as follows to measure percentage: C:0.52 ~ 0.58%, Si:1.5 ~ 1.8%, Mn:1.6 ~ 2.0%, Mo:0.18 ~ 0.24%, Ni:1.2 ~ 1.7%,
P: < 0.02%, S: < 0.02%, surplus is Fe and inevitable impurity；
The preparation method comprises the following steps:
(1) it melting: fed intake according to above-mentioned chemical component, melting and pour into ingot casting；
(2) consumable: carrying out vacuum consumable remelting for ingot casting, derives from consumption ingot；
(3) homogenizing annealing, hot rolling: consumable ingot is heated to 1150 ~ 1250 DEG C of heat preservation 50-70min homogenizing annealings, so
It hot rolling and is cooled to room temperature afterwards, obtains hot rolling bar stock；
(4) spheroidizing: after hot rolling bar stock is heated to 680 ~ 750 DEG C of 13 ~ 17 h of heat preservation, slow cooling to room temperature must anneal
Bar stock；
(5) ausrolling deforms: annealing bar stock being reheated to 880 ~ 920 DEG C of heat preservation 50-70min, is transferred to rapidly
It is cooling in 590 ~ 650 DEG C of salt bath furnaces, it is taken out after samming and carries out 3 ~ 7 passage groove rollings rapidly, control finishing temperature is not less than 540
DEG C, obtain rolled bar material；
(6) isothermal processes: rolled bar material is immediately placed in 9 ~ 11h of isothermal in 200 ~ 260 DEG C of salt bath furnace, comes out of the stove and is air-cooled to
Room temperature obtains middle carbon nanometer bainite superhigh intensity rod iron.
Preferably, controlling hot rolling finishing temperature is at 880 ~ 930 DEG C in the step (3), and slow cooling is to room temperature after bundle.
Preferably, slow cooling to room temperature is first furnace cooling to 400 DEG C in the step (4), then comes out of the stove and be air-cooled to room temperature.
Preferably, cooling temperature is controlled at 620 ~ 630 DEG C in step (5) salt bath furnace.
Preferably, roll control total deformation 30 ~ 40% in the step (5).
Preferably, step (6) salt bath furnace is controlled at 220 ~ 240 DEG C.
Further, the tensile strength of the middle carbon nanometer bainite superhigh intensity rod iron is not less than 2200MPa, hardness not
It is not less than 8.5% lower than 606HV1.0, breaking elongation.
In the chemical constituent of middle carbon nanometer bainite unimach and rod iron, C(carbon) it is that most effective solid solution is strong in steel
Change element, harden ability can be greatly improved, reduce the martensite start temperature of steel, but its too high levels will lead to steel weldability
And degraded toughness, it is too low that hardness of steel is caused to reduce；Si(silicon) precipitation that carbide in isothermal transformation can be hindered, generally contain
Amount should be higher than that 1.5wt.%, but excessively high, and toughness is caused to reduce；Mn(manganese) it is to expand austenite phase p-block element p, harden ability can be improved,
Martensite start temperature is reduced, bainite transformation temperature is reduced, refines bainite ferrite lath, excessively high Mn content is easy
Banded structure is caused, and slows down bainite transformation, the production cycle is long；Mo(molybdenum) perlitic transformation and carbide analysis can be postponed
Out, fining austenite grains reduce temper brittleness tendency, but price is higher, therefore the control of its content is in 0.18 ~ 0.24wt.%；Ni
(nickel) can expand austenite phase field, reduce the martensite start temperature of steel, improve harden ability, guarantee that overcooling austenite has
Higher stability improves toughness；P(phosphorus) and S(sulphur) be harmful element, control as far as possible it is lower, but de- P, S smelting cost compared with
Therefore height need to take into account cost and guarantee properties of product.Above-mentioned technical proposal is matched by scientific optimization chemical constituent, is produced for steel
Moral character can provide the foundation guarantee, effectively reduce martensite start temperature, improve intensity, toughness, and it is steady to improve quality
It is qualitative, guarantee the excellent of structure of steel comprehensive performance and take into account cost, selects C content range 0.52 ~ 0.58%, Si content range 1.5
~ 1.8%, Mn content range 1.6 ~ 2.0%, Mo content range 0.18 ~ 0.24%, Ni content range 1.2 ~ 1.7% control P, S content
Lower than 0.02wt.%, compared with high-carbon nanometer bainitic steel, C content is reduced the proportion, and weldability can greatly improve, and
Without adding cobalt and aluminium element, cost of alloy is substantially reduced, while also avoiding the mouth of a river caused by aluminium when continuous casting in preparation process
Blocking.
On the basis of optimizing component, preparation method has been advanced optimized, feed intake according to above-mentioned chemical component progress routine,
Melting and after pouring into ingot casting, carries out vacuum consumable remelting to remove objectionable impurities and gas componant, derives from consumption ingot.Then will
Consumable ingot is heated to 1150 ~ 1250 DEG C of heat preservation 50-70min homogenizing annealings so that ingot casting homogenization of composition, temperature are more preferable
1200 ~ 1220 DEG C, on the one hand which makes the chemical component of steel and microstructure homogenization degree high, when shortening
Between, energy consumption is totally lower；On the other hand, excessively growing up for crystal grain is avoided, refining grain size is suitable, is the equal of rod iron performance
Even stability provides good condition.It hot rolling and is cooled to room temperature after homogenizing annealing, to remove casting flaw；It is then heated to
680 ~ 750 DEG C, preferably 680-700 DEG C keep the temperature 13-17 h, then slow cooling carries out spheroidizing, make carbide spheroidization, be to room temperature
Tissue preparation is done in subsequent hot-working and heat treatment.Carry out ausrolling deformation again, i.e., further it is reheated to 880 ~
920 DEG C of heat preservation 50-70min are transferred to rapidly in 590 ~ 650 DEG C of salt bath furnaces cooling, taking-up progress 3 ~ 7 rapidly after 3-10min samming
Passage groove rolling, control finishing temperature are not less than 540 DEG C, obtain rolled bar material, and breakthrough ingenious utilize of the above method is subcooled
Ausrolling deformation leads to Austenite strengthening, to reduce martensite start temperature, and then realizes at low temperature etc.
Warm bainite transformation, and accelerate bainite transformation；Rolled bar material is immediately placed in 9 ~ 11h of isothermal in 200 ~ 260 DEG C of salt bath furnace,
9 ~ 11h of isothermal in the salt bath furnace of more accurate 220 ~ 240 DEG C of control, comes out of the stove and is air-cooled to room temperature, the isothermal shellfish under the low temperature range
The transformation of family name's body reduces bainite ferrite lath thickness, obtains nanoscale bainite structure, improves intensity, and rolling deformation
Overcooling austenite increases dislocation density, and a large amount of dislocations are hereditary to bainite ferrite, further improves intensity, final to obtain
To middle carbon nanometer bainite superhigh intensity rod iron.The lath that carbon nanometer bainite rod iron is 90-120nm by average thickness in gained
Bainite ferrite (percent by volume is 80% ~ 90%, more preferable 81% ~ 85%) and retained austenite (percent by volume for 10% ~
20%, 15% ~ 19%) composition, tensile strength reaches 2200MPa or more, hardness reaches 606HV1.0 or more, breaking elongation reaches
8.5% or more, these mechanical performance indexs have reached the level of high-carbon nanometer bainitic steel, and welding performance etc. is significantly better than height
Carbon nanometer bainitic steel.The above process also utilizes austenite deformation to accelerate bainite transformation simultaneously, shortens heat treatment cycle, improves
Technique, production efficiency, also reduce production cost.
A kind of beneficial effects of the present invention: (1) of the invention middle carbon nanometer bainite unimach and rod iron systematism
A point scientific matching is studied, the accurate preparation method of cooperation science is ingenious to strengthen with overcooling austenite rolling deformation, so that nanometer
Bainite structure, which starts transition temperature and transition temperature, to be reduced, crystal grain refinement, and dislocation retains, and tensile strength reaches 2200MPa
Above, hardness reaches 606HV1.0 or more, breaking elongation reaches 8.5% or more, has high-intensitive, high-ductility, and welding performance is good
Excellent combination mechanical property, and it is at low cost；(2) preparation method of the invention, operation is easy, is easy to control, and the production cycle is big
Big to shorten, efficiency improves, and energy consumption and cost is also effectively reduced, is advantageously implemented industrialized production.
Detailed description of the invention
Fig. 1 is the transmission electron microscope photo for the middle carbon nanometer bainite steel bar microstructure that the embodiment of the present invention 1 obtains.
Fig. 2 is the transmission electron microscope photo for the middle carbon nanometer bainite steel bar microstructure that the embodiment of the present invention 2 obtains.
Fig. 3 is the transmission electron microscope photo for the middle carbon nanometer bainite steel bar microstructure that the embodiment of the present invention 3 obtains.
Specific embodiment
Following embodiment is for middle carbon nanometer bainite unimach, rod iron and its preparation side that the present invention will be described in detail
Method and performance, to better understand the present invention.
Embodiment 1
According to chemical composition weight percent is C 0.58, Si 1.8, Mn 1.6, Mo 0.18, Ni 1.2, P 0.008, S
0.005, surplus is Fe and inevitable impurity, calculates ingredient proportion with vacuum induction furnace melting and pours into diameter
The cylindrical ingot of 180mm, then the remelting of vacuum consumable electric arc is carried out with the molten speed of 2.0kg/min, derive from consumption ingot.Consumable ingot is added
Heat carries out homogenizing annealing to 1200 DEG C of heat preservation 65min, carries out hot rolling after coming out of the stove, controls the finishing temperature of hot rolling at 880 DEG C, roll
Slow cooling obtains the hot rolling bar stock that diameter is 50mm to room temperature afterwards；Hot rolling bar stock is heated to 700 DEG C of 15 h of heat preservation progress nodularizations to move back
Fire, then furnace cooling comes out of the stove to 400 DEG C and is air-cooled to room temperature, obtains annealing bar stock；Annealing bar stock is reheated to 880 DEG C again
Heat preservation 60min comes out of the stove, and is put into rapidly in 620 DEG C of salt bath furnaces and keeps 5min cooling, samming, takes out the rapid 7 passage passes that carry out and rolls
System controls total deflection 30%, and finishing temperature is not less than 540 DEG C, obtains rolled bar material, is put into 220 DEG C of salt immediately after
Isothermal transformation 11h in liquid furnace, comes out of the stove and is air-cooled to room temperature, obtains middle carbon nanometer bainite superhigh intensity rod iron.
Detection finds that the microstructure of carbon nanometer bainite superhigh intensity rod iron is 94nm by average thickness in above-mentioned gained
Lath bainitic ferrite (percent by volume 81.1%) and retained austenite (percent by volume 18.9%) composition.According to
228.1 2010(metal material stretching test part 1 of chinese national standard GB/T: room temperature test method), measure its tension
Intensity is 2375MPa, and elongation percentage 8.5%, measurement Vickers hardness is 629HV1.0.
Embodiment 2
According to chemical component weight percentage be C 0.54, Si 1.7, Mn 1.9, Mo 0.24, Ni 1.63, P 0.005,
S 0.002, surplus are Fe and inevitable impurity, calculate ingredient proportion.With vacuum induction furnace melting, diameter is poured into
The cylindrical ingot of 180mm, then the remelting of vacuum consumable electric arc is carried out with the molten speed of 2.0kg/min, derive from consumption ingot.Consumable ingot is added
Heat carries out hot rolling after coming out of the stove to 1220 DEG C of heat preservation 55min homogenizing annealings, controls the finishing temperature of hot rolling at 900 DEG C, delays after rolling
It is cooled to room temperature, obtains the hot rolling bar stock that diameter is 50mm；Hot rolling bar stock is heated to 690 DEG C of heat preservation 15h and carries out spheroidizing, so
Furnace cooling comes out of the stove air-cooled to room temperature to 400 DEG C, obtains annealing bar stock afterwards.Annealing bar stock is reheated to 890 DEG C of heat preservations
60min comes out of the stove, and is put into rapidly in 620 DEG C of salt bath furnaces and keeps 5min, takes out and carries out 5 passage groove rollings, total deflection rapidly
40%, finishing temperature is not less than 540 DEG C, obtains rolled bar material for control, is put into isothermal in 230 DEG C of salt bath furnace immediately after and turns
Become 11h, comes out of the stove and be air-cooled to room temperature, obtain middle carbon nanometer bainite superhigh intensity rod iron.
The lath bainitic ferrite (percent by volume 84.3%) and remnants that its microstructure is 95nm by average thickness
Austenite (percent by volume 15.7%) composition.It is tried according to 228.1 2010(material during tensile of chinese national standard GB/T
Test part 1: room temperature test method), measuring tensile strength is 2290MPa, and elongation percentage 11.4%, measuring Vickers hardness is
608HV1.0。
Embodiment 3
According to chemical composition weight percent is C 0.52, Si 1.5, Mn 2.0, Mo 0.22, Ni1.7, P 0.007, S
0.004, surplus is Fe and inevitable impurity, calculates ingredient proportion with vacuum induction furnace melting and pours into diameter
The cylindrical ingot of 180mm, then the remelting of vacuum consumable electric arc is carried out with the molten speed of 2.0kg/min, derive from consumption ingot.Consumable ingot is added
Heat carries out homogenizing annealing, carries out hot rolling after coming out of the stove to 1220 DEG C of heat preservation 60min, controls the finishing temperature of hot rolling at 930 DEG C,
Rear slow cooling is rolled to room temperature, obtains the hot rolling bar stock that diameter is 50mm；After hot rolling bar stock is heated to 680 DEG C of 15 h of heat preservation, with furnace
400 DEG C are cooled to, comes out of the stove air-cooled to room temperature, obtains annealing bar stock；Annealing bar stock is reheated to 900 DEG C of heat preservation 60min to come out of the stove,
Be put into 620 DEG C of salt bath furnaces rapidly and keep 5min, take out and carry out 3 passage groove rollings rapidly, total deformation amount controlling 40%,
Finishing temperature is not less than 540 DEG C, obtains rolled bar material, is put into isothermal transformation 9h in 240 DEG C of salt bath furnace, sky of coming out of the stove immediately after
It is cooled to room temperature, obtains middle carbon nanometer bainite superhigh intensity rod iron, the lath bayesian that microstructure is 115nm by average thickness
Body ferrite (percent by volume 83.1%) and retained austenite (percent by volume 16.9%) composition.According to China national mark
Quasi- 228.1 2010(metal material stretching test part 1 of GB/T: room temperature test method), measuring tensile strength is
2200MPa, elongation percentage 13.0%.Measurement Vickers hardness is 606HV1.0.
In conclusion the preparation method of middle carbon nanometer bainite superhigh intensity rod iron provided by the invention, operates easy, appearance
Easy to control, the production cycle greatly shortens, and efficiency improves, obtained steel and rod iron, and tensile strength is high, hardness is big, breaking elongation
It is excellent, there is high-intensitive, high-ductility, the good excellent combination mechanical property of welding performance, and it is at low cost, it is advantageously implemented industry
Metaplasia produces.
Claims (8)
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