CN106086630A - A kind of tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase and manufacture method thereof - Google Patents
A kind of tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase and manufacture method thereof Download PDFInfo
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- CN106086630A CN106086630A CN201610700839.5A CN201610700839A CN106086630A CN 106086630 A CN106086630 A CN 106086630A CN 201610700839 A CN201610700839 A CN 201610700839A CN 106086630 A CN106086630 A CN 106086630A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 105
- 239000010959 steel Substances 0.000 title claims abstract description 105
- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 title claims abstract description 17
- 238000007688 edging Methods 0.000 claims abstract description 25
- 239000000203 mixture Substances 0.000 claims abstract description 19
- 238000011282 treatment Methods 0.000 claims abstract description 19
- 239000000126 substance Substances 0.000 claims abstract description 16
- 230000032683 aging Effects 0.000 claims abstract description 15
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 10
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 5
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 238000005266 casting Methods 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052787 antimony Inorganic materials 0.000 claims description 4
- 229910052785 arsenic Inorganic materials 0.000 claims description 4
- 238000005242 forging Methods 0.000 claims description 4
- 238000002156 mixing Methods 0.000 claims description 2
- 239000002994 raw material Substances 0.000 claims description 2
- 239000011159 matrix material Substances 0.000 abstract description 9
- 230000007797 corrosion Effects 0.000 abstract description 8
- 238000005260 corrosion Methods 0.000 abstract description 8
- 239000002244 precipitate Substances 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 15
- 238000009413 insulation Methods 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 11
- 239000000047 product Substances 0.000 description 11
- 238000005728 strengthening Methods 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 239000000243 solution Substances 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000003064 anti-oxidating effect Effects 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000010891 electric arc Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 238000000746 purification Methods 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910002482 Cu–Ni Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 230000001550 time effect Effects 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- 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
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a kind of tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase and manufacture method thereof, the percentage by weight of its chemical composition: Mn be 1.0 ~ 1.7 %, Ni be 2.5 ~ 4.0 %, Al be 0.5 ~ 1.5 %, Cu be 1.5 ~ 3.0%, Y be 0.01 ~ 0.10 %, C≤0.05 %, Si≤0.10 %, S≤0.04 %, P≤0.04 %, N≤0.05 %, O≤0.05 %, remaining is Fe and inevitable impurity.Solution treatment through smelting, cast and under first edging laggard row air atmosphere, then in room temperature after the edging again of total reduction 30 70 %, carry out Ageing Treatment, form Dispersed precipitate on ferrite matrix and 2 ~ 10 nm richness Cu phases and the microscopic structure of 50 100 nm richness Y phases, thus prepare tensile strength >=1020 MPa, the low cost ferrite steel plate integrating high-strength tenacity, corrosion resistance and weldability of elongation after fracture >=10 %.
Description
Technical field
The present invention relates to high-strength tough ferrite steel plate and manufacture method thereof, be specifically related to a kind of height containing nanometer precipitated phase
Tough ferrite steel plate and manufacture method thereof.
Background technology
Along with the high speed development of modernization, the requirement to high strength steel plate is more and more higher, especially petroleum pipeline, oil pipe car
Special requirement is proposed with ships armour plate etc..Traditional martensite and bainite high-strength steel meet to a certain extent to be wanted
Ask, but its high alloy content and complicated technology make high expensive, higher phosphorus content still make weldability, corrosion resistance limited.
The combination property utilizing nanometer precipitated phase strengthened mechanism to improve steel has become the important of exploitation Novel high-strength steel
Approach.Steel adds Cu, through precipitation size, quantity and the distribution of suitable Heat Treatment Control Cu nanocluster precipitated phase, by force
Change effect clearly, as patent CN104046917A, CN104046891A individually disclose " rich Cu nanocluster strengthening ",
The superhigh intensity ferritic steel of " nanocrystalline intermetallics strengthening " and manufacture method thereof.But above-mentioned two patents of invention exist as follows
Problem:
(1) not only make use of rich nanometer Cu precipitated phase to carry out reinforced ferrite matrix, also use composite Nano carbide (V, Ti,
Nb) C or (Mo, W)2C strengthens the intensity of steel, and for ensureing the strengthening effect of carbide, its carbon content is the highest, and (maximum reaches
0.2 wt.%)；
(2) more alloying element is added.In addition to Cu, Ni, Al, Mn, also add and have V, Ti, Nb(V+Ti+Nb to be not less than 0.01
%), Mo and W(Mo+W be not less than 0.05 %) and Si, B and Cr, cause cost to increase；
(3) last heat treatment is i.e. " Ageing Treatment ", and explanation is not carried out under what atmosphere.Normal air atmosphere with
Vacuum, the Ageing Treatment of protective atmosphere, not only the manufacturing cost of material there will be notable difference, and the more important thing is material
It is different that mechanical property especially fracture property there will be essence！As: design composition, the material that preparation technology is consistent with above-mentioned two patents
Material (Y.R. Wen, Y.P. Li, A. Hirata, Y. Zhang, T. Fujita, T. Furuhara, C.T. Liu,
A. Chiba, M.W. Chen. Synergistic alloying effect on microstructural evolution
and mechanical properties of Cu precipitation-strengthened ferritic alloys
mechanical properties of Cu precipitation-strengthened ferritic alloys[J].
Acta Materialia, 2013,61:7726 7740) tension failure pattern, in addition to Fe-Cu-Ni, is all fragility or solution
Reason fracture.Someone is (Z.W. Zhang, C.T. Liu, Y.R. Wen, A. Hirata, S. Guo, G. Chen, M.W.
Chen, and B. A. Chin. Influence of Aging and Thermomechanical Treatments on
the Mechanical Properties of a Nanocluster-Strengthened Ferritic Steel[J].
Metallurgical and Materials Transactions A, 2012,43A:351-359) compared for oxidation specially
Stretching fracture difference after atmosphere and vacuum aging, finds: although the cutting process before timeliness homogeneously with, but at air atmosphere and
During vacuum aging, material still occur in that obvious stretching fracture difference, i.e. vacuum aging for ductile rupture, in air atmosphere
Show the most entirely different for brittle fracture and the stress-strain diagram of the two.
In order to solve the superhigh intensity ferrum element that above-mentioned " nanocluster+nano-carbide+nanocrystalline intermetallics " is strengthened
Body steel and the high-carbon of manufacture method, many alloys and the problem of air atmosphere Ageing Treatment brittle failure, the present invention is by redesigning
Chemical composition and change manufacturing processing technic, it is thus achieved that tensile strength >=1020 MPa, elongation after fracture >=10 % collection high-strength
Toughness, corrosion resistance and weldability are in the low cost ferrite steel plate of one.
Summary of the invention
It is an object of the present invention to provide a kind of high strength and low cost containing nanometer precipitated phase tough ferrite steel plate.This
The high strength and low cost tough ferrite steel plate of invention, uniformly separates out the rich Cu phase of a large amount of a size of 2 ~ 10 nm on ferrite matrix
Rich Y phase with 50-100 nm.The strengthening of steel based on the precipitation strength of two kinds of nanometer phases, in conjunction with dislocation strengthening, refined crystalline strengthening and
Solution strengthening, forms composite toughening effect.
The present invention provides a kind of high strength and low cost containing nanometer precipitated phase tough ferrite steel plate, by weight percentage
Chemical composition is as follows: Mn be 1.0 ~ 1.7 %, Ni be 2.5 ~ 4.0 %, Al be 0.5 ~ 1.5 %, Cu be 1.5 ~ 3.0%, Y be 0.01 ~
0.10 %, C≤0.05 %, Si≤0.10 %, S≤0.04 %, P≤0.04 %, N≤0.05 %, O≤0.05 %, remaining is Fe
With inevitable impurity.
Described nanometer precipitated phase is rich Cu phase and the rich Y phase of 50-100 nm, every cu μ m of a size of 2 ~ 10 nm
Nanometer phase amount is 5 × 104 ~ 8×106Individual, wherein rich Y phase accounts for 0.2 ~ 2 %.
The described element in rich Cu phase is based on Cu, possibly together with Ni, Al, Mn element；The described element in rich Y phase with
Y is main, possibly together with Ni, Al, Mn and As, Sb element.
Further object is that offer is a kind of and manufacture the above-mentioned high strength and low cost tough iron containing nanometer precipitated phase
The method of ferritic steel plate.
A kind of method manufacturing the above-mentioned high strength and low cost containing nanometer precipitated phase tough ferrite steel plate, step is as follows:
(1) after the raw material mixing of the chemical composition meeting the aforementioned high strength and low cost containing nanometer precipitated phase tough ferrite steel plate,
Ingot casting after the smelting of smelting stove, air cooling to room temperature, the thickness of ingot casting is more than 10 times of finished steel plate thickness；
(2) after ingot casting is heated to 1050-1100 DEG C and is incubated uniformly, first edging becomes base, and water-cooled is to room temperature, and first finish to gauge forging is controlled
Make at 900-950 DEG C, 1.5-3.0 times that thickness is finished steel plate thickness of first edging base；
(3) first edging base is after 900-950 DEG C of air atmosphere solution treatment, and water-cooled is to room temperature；
(4) the first edging base after solution treatment is in room temperature after the edging again of total reduction 30-70 %, and water-cooled is to room temperature；
(5) base of edging again after water-cooled is after 500-600 DEG C of air atmosphere Ageing Treatment 17-24 hour, water-cooled to room temperature, system
The high strength and low cost tough ferrite steel plate of nanometer precipitated phase is contained described in.
The inventive method combines Ultra-low carbon, the antioxidation of Y and purification, prepares tensile strength >=1020 MPa, has no progeny
The low cost ferrite steel plate integrating high-strength tenacity, corrosion resistance and weldability of percentage elongation >=10 %.
Beneficial effects of the present invention is as follows:
1) effect of addition element Y in steel plate of the present invention: separate out mutually with rich Y nanometer, plays precipitation strength and thin brilliant effect；Make steel
Oxide skin is thin and is tightly combined with matrix, and the ageing resistance oxidation of steel and corrosion resistance significantly improve；Make the harmful element enrichments such as As, Sb
Around rich Y phase, form nanometer mixed phase, effectively purified steel.
2) undersized rich nanometer Cu combines the most large-sized rich nanometer Y phase, can take into account obdurability, make steel plate of the present invention
Tensile strength >=1020 MPa, elongation after fracture >=10 %.
3) C content ultralow (≤0.05 wt.%), improves the weldability of steel plate, toughness and corrosion resistance.
4) without carbide former V, Ti, Nb, Mo and W；Solid solution and Ageing Treatment are all carried out in air atmosphere,
Without vacuum or protective atmosphere, technique is simple and convenient to operate, and makes the cost of invention steel reduce further.
In a word, by Reasonable Regulation And Control Cu, Ni, Al, Mn, Si, Y content, control C content, at solid solution, deformation and timeliness
Reason, forms Dispersed precipitate on ferrite matrix and the rich Cu phase of 2 ~ 10 nm and the organizational structure of the rich Y phase of 50-100 nm；Fully
Play the antioxidation of Y element, purification and thin brilliant effect, solve " chemical combination between nanocluster+nano-carbide+nano metal
Thing " the superhigh intensity ferritic steel strengthened and the high-carbon of manufacture method thereof, many alloys, the asking of air atmosphere Ageing Treatment brittle failure
Topic, prepared tensile strength >=1020 MPa, elongation after fracture >=10 % integrate high-strength tenacity, corrosion resistance and weldability
Low cost ferrite steel plate, can be widely applied to ships, automobile, pipeline, bridge, pressure vessel, ocean engineering, engineering machinery
In field.
Accompanying drawing explanation
Fig. 1 is the matrix of the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase that the embodiment of the present invention 1 manufactures
The replica transmission electron microscope photo of middle rich Y nanometer phase；
Fig. 2 be the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase that the embodiment of the present invention 1 manufactures matrix in rich Y
The replica transmission electron microscope of nanometer phase and corresponding energy spectrogram；
Fig. 3 be the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase that the embodiment of the present invention 1 manufactures matrix in rich
The thin film high-resolution-ration transmission electric-lens photo of Cu nanometer phase；
Fig. 4 is the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase and the comparative example sky of the embodiment of the present invention 4 manufacture
The stereoscan photograph of gas atmosphere timeliness rear surface iron scale；
Fig. 5 is the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase and the comparative example sky of the embodiment of the present invention 4 manufacture
The stereoscan photograph of gas atmosphere timeliness after-drawing fracture.
Detailed description of the invention
Below in conjunction with specific embodiment, technical scheme is further illustrated.
The present invention provides a kind of high strength and low cost containing nanometer precipitated phase tough ferrite steel plate, by weight percentage
Chemical composition: Mn be 1.0 ~ 1.7 %, Ni be 2.5 ~ 4.0 %, Al be 0.5 ~ 1.5 %, Cu be 1.5 ~ 3.0%, Y be 0.01 ~ 0.10
%, C≤0.05 %, Si≤0.10 %, S≤0.04 %, P≤0.04 %, N≤0.05 %, O≤0.05 %, remaining is Fe and can not
Avoid impurity.
Below to the described high strength and low cost containing nanometer precipitated phase each chemical composition content range of tough ferrite steel plate
Restriction reason explain:
C: for ensureing superior weldability energy and the toughness of steel, use ultralow carbon content.The C content of the present invention is not higher than 0.05
wt.%。
The nanometer precipitated phase of Cu: the present invention mainly comprises element, utilizes lower-cost Cu to form disperse nanometer precipitated phase
Can efficient hardening ferritic steel；Additionally, Cu also can improve steel corrosion resistance in air and sea water.Cu content is too low, and strengthening is made
With weak, and Cu too high levels, it is easily generated hot-short, so the content of Cu is limited to 1.5 ~ 3.0 % in steel of the present invention.
Ni: one of component of nanometer precipitated phase, participates in the invigoration effect of nanometer precipitated phase, and nanometer can be hindered to separate out
Growing up of phase；Ni also can improve the toughness of steel.But Ni too high levels, meeting retained austenite and increase production cost in steel, this
The content of bright Ni is limited to 2.5 ~ 4.0%.
Mn: one of component of nanometer precipitated phase, participates in the invigoration effect of nanometer precipitated phase.Mn is conducive to refinement ferrum element
Body crystal grain, improves the obdurability of steel, but Mn amount is too high, has retained austenite and cause segregation, poor toughness and weldability in steel
Low, the content of Mn of the present invention is limited to 1.0 ~ 1.7 %.
Al: one of component of nanometer precipitated phase, participates in the invigoration effect of nanometer precipitated phase.Al participates in deoxidation but content
Too high, cause casting difficulty, the content of Al of the present invention is limited to 0.5 ~ 1.5 %.
Another nanometer precipitated phase of Y: the present invention mainly comprise element, participate in the invigoration effect of nanometer precipitated phase.This
The C amount of bright steel is ultralow, adds Y and forms rich Y nanometer precipitated phase replacement Carbide Precipitation phase in the base；Y makes harmful unit such as As, Sb
Element is enriched in around rich Y phase, forms nanometer mixed phase, has effectively purified steel；Y adds in steel, have impact on the diffusion of O and Fe,
The oxide skin that steel is thermally formed in air atmosphere is thin and is tightly combined with matrix, and the ageing resistance that improve steel aoxidizes and resistance to
Erosion property.Owing to Y is rare metal, too high content does not only result in cost to be increased, and easily segregation forms bigger granule, therefore
The content of Y of the present invention is limited to 0.01 ~ 0.10 %.
Si: dissolve in ferrite, plays solution strengthening effect.Too much can reduce the toughness of steel, the content of Si of the present invention is limited to
0-0.1 %。
S and P: inevitable impurity element in steel, reduces as far as possible, the present invention limit S≤0.04 %, P in steel≤
0.04 %。
N and O: inevitable impurity element in steel, the harm toughness of steel and weldability, the present invention limit N in steel≤
0.05 %、O≤0.05 %。
The present invention also provides for a kind of method manufacturing the described high strength and low cost tough ferrite steel plate containing nanometer precipitated phase,
The step of its manufacture method is as follows:
(1) raw mixture that the chemical composition of a kind of high strength and low cost containing nanometer precipitated phase tough ferrite steel plate is constituted,
Smelting stove smelt after ingot casting, air cooling to room temperature, the thickness of ingot casting be 10 times of finished steel plate thickness or more than；
(2) after ingot casting is heated to 1050-1100 DEG C and is incubated uniformly, first edging becomes base, and water-cooled is to room temperature, and first finish to gauge forging is controlled
Make at 900-950 DEG C, 1.5-3.0 times that thickness is finished steel plate thickness of first edging base；
(3) first edging base is after 900-950 DEG C of air atmosphere solution treatment, and water-cooled is to room temperature；
(4) the first edging base after solution treatment is in room temperature after the edging again of total reduction 30-70%, and water-cooled is to room temperature；
(5) base of edging again after water-cooled is after 500-600 DEG C of air atmosphere Ageing Treatment 17-24 hour, water-cooled to room temperature, system
The high strength and low cost tough ferrite steel plate of nanometer precipitated phase is contained described in.
A kind of method manufacturing the described high strength and low cost tough ferrite steel plate containing nanometer precipitated phase of the present invention,
Can use the melting raw mixtures such as induction furnace, converter, electric arc furnace, then can use the mode of molding or continuous casting formed steel ingot or
Continuous casting billet.The thickness of steel ingot or continuous casting billet be into 10 times of base steel plate thickness or more than, with ensure finished steel plate deformation uniformly and
There is thin brilliant effect.After steel ingot or continuous casting billet are heated to 1050-1100 DEG C of scope and insulation uniformly, roll for the first time or be forged into
Slab, the final temperature of first rolling or forging controls at 900-950 DEG C, and then water-cooled is to room temperature.The thickness of first edging base
For 1.5-3.0 times of finished steel plate thickness, to ensure follow-up dislocation strengthening requirement.First edging base is again through 900-950 DEG C of sky
After gas atmosphere solution treatment, water-cooled is to room temperature, and the first edging base after solution treatment is in room temperature through total reduction 30-70 % again
Secondary edging, water-cooled is to room temperature.Control 30-70 % total reduction be to ensure that enough dislocation densities, strengthen next step time
Effect separates out effect, also for avoiding the formation of too strong texture.The base of edging again after water-cooled is when 500-600 DEG C of air atmosphere
After effect processes 17-24 hour, water-cooled to room temperature, prepare the described high strength and low cost tough ferrite steel plate containing nanometer precipitated phase.
The present invention is described in further detail by the following examples.
Embodiment 1
Manufacturing step:
1) chemical composition smelting molten steel in vaccum sensitive stove of the embodiment 1 as shown in table 1, is molded into steel ingot, and air cooling is to room
Temperature.The thickness of steel ingot is 300 mm.
2) after Heating Steel Ingots to 1100 DEG C insulation 1.5 h, multistage hot deformation, start rolling temperature 1050 DEG C are started.When rolled piece is thick
When degree is 7 mm, terminating rolling, finishing temperature 920 DEG C, rolled piece water-cooled is to room temperature.
3) rolled piece is heated in air atmosphere 900 DEG C, be incubated after 0.5 h immediately water-cooled to room temperature.Then by rolled piece
After room temperature is rolled to finished product thickness 2.5 mm, water-cooled is to room temperature.
4) steel plate after room temperature being rolled, is heated to 550 DEG C of insulation 17 h in air atmosphere, and insulation terminates rear water-cooled to room
Temperature, prepares finished product rolled plate.
5) the rich Cu phase separated out in finished product rolled plate and the average-size of rich Y phase are respectively 6 nm and 80 nm.Rich Cu
The composition of phase is (wt.%): 5.45Al, 4.90Mn, 23.54Fe, 20.68Ni, 45.13Cu, 0.29Y；Rich Y phase is: 18.08Al,
19.66Ni, 27.58Y, 9.34Cu, 10.96As, 12.86Sb, 1.15Mn, 0.38Fe.Every cu μ m nanometer phase amount 8 ×
106Individual, wherein rich Y phase accounts for 1.5 %.
Embodiment 2
Manufacturing step:
1) chemical composition smelting molten steel in electric arc furnace of the embodiment 2 as shown in table 1, is molded into steel ingot, and air cooling is to room temperature.Steel
The thickness of ingot is 200mm.
2) after Heating Steel Ingots to 1080 DEG C insulation 1.8 h, multistage hot deformation, start rolling temperature 1030 DEG C are started.When rolled piece is thick
When degree is 6 mm, terminating rolling, finishing temperature 900 DEG C, rolled piece water-cooled is to room temperature.
3) rolled piece is heated in air atmosphere 920 DEG C, be incubated after 0.5 h immediately water-cooled to room temperature.Then by rolled piece
After room temperature is rolled to finished product thickness 2.0 mm, water-cooled is to room temperature.
4) steel plate after room temperature being rolled, is heated to 580 DEG C of insulation 20 h in air atmosphere, and insulation terminates rear water-cooled to room
Temperature, prepares finished product rolled plate.
5) the rich Cu phase separated out in finished product rolled plate and the average-size of rich Y phase are respectively 10 nm and 99 nm.Often stand
Side's micron/nano phase amount is 5 × 104Individual, wherein rich Y phase accounts for 2 %.
Embodiment 3
Manufacturing step:
1) chemical composition smelting molten steel in induction furnace of the embodiment 3 as shown in table 1, is molded into steel ingot, and air cooling is to room temperature.Steel
The thickness of ingot is 100mm.
2) after Heating Steel Ingots to 1050 DEG C insulation 2.0 h, multistage hot deformation, start rolling temperature 1010 DEG C are started.When rolled piece is thick
When degree is 3 mm, terminating rolling, finishing temperature 905 DEG C, rolled piece water-cooled is to room temperature.
3) rolled piece is heated in air atmosphere 945 DEG C, be incubated after 0.5 h immediately water-cooled to room temperature.Then by rolled piece
After room temperature is rolled to finished product thickness 1.0 mm, water-cooled is to room temperature.
4) steel plate after room temperature being rolled, is heated to 500 DEG C of insulation 24 h in air atmosphere, and insulation terminates rear water-cooled to room
Temperature, prepares finished product rolled plate.
5) the rich Cu phase separated out in finished product rolled plate and the average-size of rich Y phase are respectively 2 nm and 50 nm.Often stand
Side's micron/nano phase amount is 9 × 105Individual, wherein rich Y phase accounts for 0.2 %.
Table 1 invention steel embodiment and the chemical composition (percentage by weight) of comparative example
| Numbering | Cu | Ni | Al | Mn | Y | C | Si | Fe |
| Embodiment 1 | 2.70 | 3.85 | 1.10 | 1.50 | 0.08 | 0.03 | 0.07 | Surplus |
| Embodiment 2 | 1.90 | 4.00 | 1.00 | 1.60 | 0.10 | 0.03 | 0.05 | Surplus |
| Embodiment 3 | 3.00 | 2.90 | 1.50 | 1.20 | 0.02 | 0.04 | 0.03 | Surplus |
| Embodiment 4 | 2.50 | 4.00 | 1.00 | 1.50 | 0.06 | 0.04 | 0.04 | Surplus |
| Embodiment 5 | 2.50 | 4.00 | 1.00 | 1.50 | 0.01 | 0.05 | 0.04 | Surplus |
| Embodiment 6 | 2.50 | 4.00 | 1.00 | 1.50 | 0.04 | 0.04 | 0.03 | Surplus |
| Comparative example | 2.50 | 4.00 | 1.00 | 1.50 | 0 | 0.05 | 0.04 | Surplus |
Embodiment 4,5,6 and comparative example
The chemical composition of embodiment 4,5,6 and comparative example is in addition to Y, basically identical.Embodiment 4,5,6 walks with the reality manufacture of comparative example
Rapid as follows:
1) embodiment 4,5,6 as shown in table 1 and chemical composition smelting molten steel in vaccum sensitive stove of comparative example, be molded into steel
Ingot, air cooling is to room temperature.The thickness of steel ingot is 200mm.
2) after Heating Steel Ingots to 1100 DEG C insulation 2 h, multistage hot deformation, start rolling temperature 1050 DEG C are started.When rolled piece thickness
When being 4 mm, terminating rolling, finishing temperature 900 DEG C, rolled piece water-cooled is to room temperature.
3) rolled piece is heated in air atmosphere 900 DEG C, be incubated after 0.5 h immediately water-cooled to room temperature.Then by rolled piece
After room temperature is rolled to finished product thickness 1.5 mm, water-cooled is to room temperature.
4) steel plate after room temperature being rolled, is heated to 550 DEG C of insulation 17 h in air atmosphere, and insulation terminates rear water-cooled to room
Temperature, prepares finished product rolled plate.
Table 2 lists the mechanical property of all embodiments of the invention and comparative example.
Table 2 invention steel embodiment and the mechanical property of comparative example
| Numbering | Tensile strength/MPa | Have no progeny elongation/% |
| Embodiment 1 | 1120 | 12 |
| Embodiment 2 | 1050 | 14 |
| Embodiment 3 | 1200 | 10 |
| Embodiment 4 | 1090 | 12 |
| Embodiment 5 | 1020 | 13 |
| Embodiment 6 | 1050 | 13 |
| Comparative example | 1000 | 10 |
Claims (4)
1. the high strength and low cost tough ferrite steel plate containing nanometer precipitated phase, it is characterised in that by weight percentage
Chemical composition is as follows: Mn be 1.0 ~ 1.7 %, Ni be 2.5 ~ 4.0 %, Al be 0.5 ~ 1.5 %, Cu be 1.5 ~ 3.0%, Y be 0.01 ~
0.10 %, C≤0.05 %, Si≤0.10 %, S≤0.04 %, P≤0.04 %, N≤0.05 %, O≤0.05 %, remaining is Fe
With inevitable impurity.
High strength and low cost the most according to claim 1 tough ferrite steel plate, it is characterised in that described nanometer precipitated phase is
The rich Cu phase of a size of 2 ~ 10 nm and the rich Y phase of 50-100 nm, every cu μ m nanometer phase amount is 5 × 104 ~ 8×106
Individual, wherein rich Y phase accounts for 0.2 ~ 2 %.
High strength and low cost the most according to claim 2 tough ferrite steel plate, it is characterised in that the shown unit in rich Cu phase
Element is based on Cu, possibly together with Ni, Al, Mn element；The described element in rich Y phase based on Y, possibly together with Ni, Al, Mn and
As, Sb element.
4. the manufacture method of the tough ferrite steel plate of the high strength and low cost containing nanometer precipitated phase described in claim 1, its feature
Being, step is as follows:
(1) after the raw material mixing of the chemical composition meeting the aforementioned high strength and low cost containing nanometer precipitated phase tough ferrite steel plate,
Ingot casting after the smelting of smelting stove, air cooling to room temperature, the thickness of ingot casting is more than 10 times of finished steel plate thickness；
(2) after ingot casting is heated to 1050-1100 DEG C and is incubated uniformly, first edging becomes base, and water-cooled is to room temperature, and first finish to gauge forging is controlled
Make at 900-950 DEG C, 1.5-3.0 times that thickness is finished steel plate thickness of first edging base；
(3) first edging base is after 900-950 DEG C of air atmosphere solution treatment, and water-cooled is to room temperature；
(4) the first edging base after solution treatment is in room temperature after the edging again of total reduction 30-70 %, and water-cooled is to room temperature；
(5) base of edging again after water-cooled is after 500-600 DEG C of air atmosphere Ageing Treatment 17-24 hour, water-cooled to room temperature, system
The high strength and low cost tough ferrite steel plate of nanometer precipitated phase is contained described in.
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| CN107201435A (en) * | 2017-04-29 | 2017-09-26 | 天津大学 | With nanocluster and dislocation, the preparation method of the ferrous alloy of twins sub-structure |
| CN112522618A (en) * | 2020-11-24 | 2021-03-19 | 首钢集团有限公司 | Full-ferrite high-strength steel and preparation method thereof |
| CN114540708A (en) * | 2022-02-14 | 2022-05-27 | 厦门大学 | Co-rich nanoparticle reinforced ferrite stainless steel and preparation method thereof |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN107201435A (en) * | 2017-04-29 | 2017-09-26 | 天津大学 | With nanocluster and dislocation, the preparation method of the ferrous alloy of twins sub-structure |
| CN107201435B (en) * | 2017-04-29 | 2019-01-11 | 天津大学 | The preparation method of ferrous alloy with nanocluster and dislocation, twins sub-structure |
| CN112522618A (en) * | 2020-11-24 | 2021-03-19 | 首钢集团有限公司 | Full-ferrite high-strength steel and preparation method thereof |
| CN112522618B (en) * | 2020-11-24 | 2022-02-18 | 首钢集团有限公司 | Full-ferrite high-strength steel and preparation method thereof |
| CN114540708A (en) * | 2022-02-14 | 2022-05-27 | 厦门大学 | Co-rich nanoparticle reinforced ferrite stainless steel and preparation method thereof |
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Effective date of registration: 20231204 Address after: 436000 Tuanshan Village, Yangye Town, Ezhou City, Hubei Province Patentee after: HUBEI SHILI MOULD MATERIAL CO.,LTD. Address before: 430081 construction of Qingshan District, Hubei, Wuhan Patentee before: WUHAN University OF SCIENCE AND TECHNOLOGY |