CN103339279B - Have the high Mn content steel of high mechanical resistance and formability manufacture method and can thus obtained steel - Google Patents
Have the high Mn content steel of high mechanical resistance and formability manufacture method and can thus obtained steel Download PDFInfo
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- CN103339279B CN103339279B CN201180066940.5A CN201180066940A CN103339279B CN 103339279 B CN103339279 B CN 103339279B CN 201180066940 A CN201180066940 A CN 201180066940A CN 103339279 B CN103339279 B CN 103339279B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 47
- 239000010959 steel Substances 0.000 title claims abstract description 47
- 238000000034 method Methods 0.000 title claims abstract description 26
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 239000000126 substance Substances 0.000 claims abstract description 5
- 238000000137 annealing Methods 0.000 claims description 21
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 16
- 230000000694 effects Effects 0.000 claims description 13
- 229910001566 austenite Inorganic materials 0.000 claims description 12
- 238000005275 alloying Methods 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 229910045601 alloy Inorganic materials 0.000 claims description 5
- 239000000956 alloy Substances 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 239000011248 coating agent Substances 0.000 claims description 5
- 238000000576 coating method Methods 0.000 claims description 5
- 229910052739 hydrogen Inorganic materials 0.000 claims description 5
- 239000001257 hydrogen Substances 0.000 claims description 5
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 3
- 238000005097 cold rolling Methods 0.000 claims description 3
- 239000013078 crystal Substances 0.000 claims description 3
- 229910052749 magnesium Inorganic materials 0.000 claims description 3
- 239000011777 magnesium Substances 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 239000011701 zinc Substances 0.000 claims description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 2
- 239000010931 gold Substances 0.000 claims description 2
- 229910052737 gold Inorganic materials 0.000 claims description 2
- 230000006698 induction Effects 0.000 claims description 2
- 238000002360 preparation method Methods 0.000 claims 1
- 229910000937 TWIP steel Inorganic materials 0.000 abstract description 13
- 230000008569 process Effects 0.000 abstract description 2
- 239000011572 manganese Substances 0.000 description 14
- 239000000047 product Substances 0.000 description 6
- 125000004429 atom Chemical group 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 230000007246 mechanism Effects 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 230000004913 activation Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000001419 dependent effect Effects 0.000 description 2
- 230000003993 interaction Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000011017 operating method Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 235000013399 edible fruits Nutrition 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000003779 hair growth Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 229910052702 rhenium Inorganic materials 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000009865 steel metallurgy Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
Classifications
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/56—Continuous furnaces for strip or wire
- C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- 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 Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Subject of the present invention is a kind of method producing austenitic steel with high mechanical resistance and formability.The steel proposed has following chemical composition, by weight percentage: C0.2 1.5；Mn10‑25；Optionally Ni < 2；0.05‑2.00；A10.01‑2.0；N<0.1；P+Sn+Sb+As<0.2；S+Se+Te<0.5；And optionally Nb+Co < 1 and/or Re+W < 1, in addition to inevitable impurity, remaining is Fe, and processes through specific full annealed.Another theme of the present invention is can thus obtained austenitic steel product and the purposes in car industry thereof.Fig. 2 is shown as the TWIP steel of present invention micro structure after deformation, wherein observes twin existence.
Description
Technical field
The present invention relates to, by what high Mn content austenitic steel manufactured, there is high mechanical resistance and high formability
The field (referred to as TWIP steel, i.e. twinning-induced plasticity steel) of product.
Background technology
High Mn content TWIP shaped steel belongs to the steel that in height endurability rings territory, a class is unique, it is characterized by display
Unique engineering properties.TWIP shaped steel has face-centered cubic lattice (FCC) and low stacking fault energy (SFE)
Austenitic structure, it can promote the activation of twin Deformation Mechanisms (twin of mechanical induction).
In a metal, two kinds of basic and emulative mechanism that plastic deformation occurs are dislocation movement by slip and become dimorphism
Become (twin) (gemination).
Preferential by the steel of twin deformation in order to obtain, it is necessary to steel to be carried out metallurgical design so that solute
Composition is suitable to increase the shear stress to dislocation movement by slip simultaneously and reduce stacking fault energy (SFE).
The atom of solute is interacted by two kinds of mechanism with dislocation:
1) interaction between solute and dislocation produces netted deformation.This interaction is to a certain extent
Relevant with the size difference between solute and solvent atom.The atom substituted is reducing near the position of dislocation line
Stress state: thus cause needing bigger tension force ability moving dislocation.
2) in face-centered cubic lattice (FCC), (low stacking fault energy), common dislocation in defined conditions
Become unstable and tend to be divided into 2 partial dislocations (Xiao Keli dislocation (Shockley
dislocations)).The feature of the lattice region between two partial dislocations is a kind of entitled stacking defect
Fault of construction, the normal sequence of crystal microchip of namely height stacking changes, brilliant from face-centered cubic
The type sequence of lattice (FCC) becomes the type sequence of close-packed hexagonal lattice (HCP).Under equilibrium state,
In stacking defect area, the concentration of solute is tended to more than meansigma methods.This uneven solute atoms be distributed into
One step enhances the ability (suzuki effect) of anti-dislocation movement by slip.
Typical true stress-logarithmic strain the curve of TWIP steel is segmented into three sections:
1st section: in the beginning of plastic period, deformation is mainly occurred by dislocation movement by slip.
2nd section: along with deformation and relative shear stress increase because of hardened material, need compared with dislocation movement by slip
The twin process of the activation energy of the most constant (unrelated with deformation) that will be bigger gradually starts.Thus exist
Deformation threshold value, main by twin generation in threshold value material deformation further above.This threshold value can be by closing
Suitable steel metallurgy design controls.For still in the deformation increased, twin carry out deforming and this causes
Distinctive high ductibility TWIP effect.Twin tension force for the fact produced by the dependent/non-dependent of deformation is,
Deformation the most uniformly occurs and does not has constriction (high uniformity stretching).
3rd section: when deformation reaches high level, twin also it is obstructed, inhomogeneous deformation occurs from this point on,
And localized necking causes fracture occur.
It is known that this TWIP die, the most band-shaped, paid attention to especially in automotive field.Thing
In reality, TWIP steel band can be used to manufacture the automobile component of complicated shape in a relatively simple manner and at needs
Use under conditions of high-mechanical property, especially relate to energy absorption and structure-reinforced parts.
According to the situation of this area, exist in automotive field some be intended to obtain to show high engineering properties and
It is adapted to provide for the scheme proposals of the TWIP steel of the performance of above-mentioned report.
United States Patent (USP) 2010258212 proposes the method producing high stretch TWIP shaped steel, relates to controlling
Initial steel forms, and particularly control is as the content (4.0-5.0%) of the titanium of required alloying element.
But, according to known technique, between formability and mechanical resistance, and the stablizing of austenite phase
From the perspective of reaching optimum balance between property and the surface quality of product obtained, there is not yet and make us completely
Satisfied method.
Thus need to provide the production method of a kind of TWIP steel at specific area, in order in mechanical resistance and
Optimum balance is reached between formability and great surface quality.
Summary of the invention
The method of the present invention meets this requirement, this method proposes by controlling chemical composition and heat treatment step
Suddenly the condition of the stability of austenite phase is realized.
Therefore, subject of the present invention is to produce TWIP (twinning-induced plasticity) shaped steel of high Mn content
Method, described steel has high mechanical resistance and formability, has the change that following percentage by weight represents
Learn and form:
C 0.2-1.5；Mn 10-25；Optionally Ni < 2；Si 0.05-2.00；Al 0.01-2.0；N<0.1；
P+Sn+Sb+As<0.2；S+Se+Te<0.5；And optionally Nb+Co < l and/or Re+W < l, except not
Outside evitable impurity, remaining is Fe, after the most cold rolling, within the temperature range of 900 DEG C-1100 DEG C continuously
Carry out full annealed, the time between 60 seconds to 120 seconds, or within the temperature range of 700 DEG C-800 DEG C
Full annealed is conducted batch-wise, the time between 30 minutes to 400 minutes, carbon activity a of annealing atmospherec
Between 0.1 and 1.0, for continuous annealing, nitrogen N2Content is between 90% and 100%, for dividing
Criticizing annealing, nitrogen content is between 0% and 100%, and for continuous annealing, hydrogen content is 0% and 10%
Between, for batch annealing, hydrogen content is between 0% and 100%, and dew point less than 0 DEG C and preferably exists
Between-10 DEG C and-50 DEG C.
The scope that preferably constitutes of the combination of single alloying element or alloying element is independently of each other:
C 0.4-0.8；Mn 16-19；Optionally Ni < 1.0；Si 0.2-0.4；Al 0.1-1.5；N 0.01-0.05；
And optionally Nb+Co 0.1-0.4 and/or Re+W 0.3-0.7.
According to an embodiment, the method for proposition also includes using the alloy containing magnesium and aluminum based on zinc to exist
The further operating procedure of metal coating is formed on the hot steel band obtained.
Another theme of the present invention is uncoated austenite TWIP steel, can be obtained as described above, under having
The mechanical property in face:
Rp0.2 between 250 and 350MPa
Rm between 850 and 1100MPa
A80 between 60% and 100%.
It is above-mentioned based on zinc containing magnesium with the conjunction of aluminum that the further operating procedure that can use above-mentioned report obtains
The austenitic steel of gold coating is also subject of the present invention.
It is optionally coated with the steel of kirsite according to the present invention and can be used in the production of complicated form part, this portion
Part is used for energy absorption, structure-reinforced and general mobile applications.
According to the present invention be optionally coated with kirsite austenite TWIP steel can with band, plate, rod, base
Part, the form of tubing use.
Finally, the Mn high-load steel as the raw material of said method is also another theme of the present invention.
The metallurgy action played according to the various alloying elements of the TWIP steel of the present invention can be distinguished at least 4
The effect that kind is different:
1) stability of face-centered cubic lattice (FCC) austenite phase.Alloying element Mn and C is for this effect
Fruit plays Main Function.
2) stacking fault energy (SFE) is controlled.In order to make steel obtain optimal ductility, the optimal energy of stacking fault energy
Scope is 20-40mJ/m2.Alloying element Mn and C, and together with Al with Si, this effect is played main
Act on.
3) by plastic deformation threshold optimization TWIP character, from the beginning of this threshold value, deformation is almost exclusively by double
Hair growth promoting is raw.Large scale atom such as Nb, Co, the Re of the percentage ratio that this effect can be normally limited
Finely control with W.
4) some elements, including Al, when adding fashionable with suitable amount, in addition to the effect to SFE,
Also tend to resist the formation of HCP martensite when alloy deformation.
The function of single alloying element, and the specifically chosen reason of the bound of relative weight percents,
Hereinafter explain.
Carbon is stablized for austenite and is made contributions.The scope of its composition is 0.2-1.5%.
When C is less than 0.2%, in steel is processed, observe that crackle is formed.When C is higher than 1.5%, observe
To relatively low formability.
It addition, manganese plays decisive role in the stabilisation of austenite phase.The scope of its composition is according to this
Bright is 16-18%.Corresponding to this Mn percentage-proportion interval, it was observed that the maximum stability of austenite.
Silicon plays mechanical resistance and the function of ductility increasing steel.Si content 0.05% and 2.0% it
Between.When its percentage ratio is less than 0.05%, forms thick manganese and the oxide skin(coating) of ferrum, cause pickling time to increase
Add, and the surface quality of the corrosion resistance of annealed steel and cold-reduced sheet declines.When its percentage ratio is higher than 2.0%,
The stability of steel declines.
The existence of aluminum finally determines, to increase the ductility of steel.It is according in the austenitic steel of the present invention
Content is between 0.01% and 2.0%.When the content of Al is less than 0.01%, mechanical resistance increases, but
It is to occur that ductility quickly reduces.On the contrary, when its percentage ratio is higher than 2.0%, steel shows the extension of reduction
Property and castability relatively low in continuously casting, and the susceptibility-to-corrosion in hot rolling, result makes products obtained therefrom
Poor surface quality.
Nitrogen is promoted by the precipitation (in solidification) with the reactive aluminum in austenite crystal and fine nitride
Twin generation, there is the mechanical resistance and the appropriate degree of elongation improved in steel processing in it.Nitrogen is being pressed
Present in steel according to present invention use, percentage ratio is less than 0.1%.It is true that when the content of N is higher than 0.1%
Time, there is the nitrides precipitate of excess, cause the reduction of cold machining and formability.
Nb+Co and Re+W promotes twin formation, and improves the mechanical resistance in steel processing and elongation
Appropriate degree.
By the experimental activity as present invention basis, it has been found that in order to control non-decarburization or carburetting, control
In atmosphere of annealing furnace, the activity of carbon is very important.So far the overall description to the present invention is had been provided for.?
Under following figure and the auxiliary of embodiment, more detailed description to its embodiment is provided below, in order to
It is more fully understood that its target, feature and advantage.
Accompanying drawing explanation
Fig. 1 is shown as the micro structure of the undeformed TWIP steel of the embodiment of the present invention 2.
Fig. 2 is shown as the TWIP steel of the embodiment of the present invention 2 micro structure after deformation, wherein observes
Twin existence.
Detailed description of the invention
Embodiment 1
According to the method for the present invention, the steel containing following component is processed: except ferrum and the most miscellaneous
Beyond matter, containing C 0.6；Mn 18；Ni 0.5；0.3；Al 1.0；P+Sn+Sb+As 0.1；S+Se+Te
0.01；N 0.05；Nb+Co 0.1.
Use casting apparatus to obtain the steel band thick for 1.0mm requiring patent protection, to its carry out hot rolling,
Cold rolling, and carry out full annealed according to the method for reported be-low.
Continuous recrystallization annealing occurs 90 seconds, in annealing atmosphere at 1000 DEG C in the atmosphere of non-decarburization
Carbon activity is 0.15, nitrogen content 100%, dew point-25 DEG C.
Final products show following mechanical property: Rp0.2 290MPa, Rm 1000MPa and A80
90%, and there is austenite microstructure.
This product is for manufacturing the high mechanical resistance of needs and the automobile component of high formability, such as vehicle structure
Part.
Embodiment 2
According to the method for the present invention, the steel containing following component is processed: except ferrum and the most miscellaneous
Beyond matter, containing C 0.6；Mn 17；Si 0.3；Al 0.04；P+Sn+Sb+As<0.1；S+Se+Te 0.01；
N 0.05；Re+W 0.2.
The steel pipe thick for the 2.0mm that makes of this steel using casting apparatus to obtain is carried out hot rolling, cold
Roll, and carry out full annealed according to the method for reported be-low.
Full annealed is carried out 180 minutes at 750 DEG C in batches.Carbon activity in annealing atmosphere is 0.15,
Nitrogen percentage ratio in stove is 95%, and dew point is-30 DEG C, hydrogen 5%.
Final steel band shows following mechanical property: Rp0.2 310MPa, Rm 950MPa and A80
80%, and there is austenite microstructure.
This product is for manufacturing the high mechanical resistance of needs and the automobile component of high ductibility, such as vehicle structure
Reinforcing bar.
Embodiment 3
In this comparative example, the method according to the present invention from embodiment 1 and embodiment 2 obtains
TWIP steel with the TRIP 800 made comparisons, HSLA S700MC and DP 980 steel with regard to engineering properties, micro-knot
Structure and offer condition compare.
Result of the comparison is in the following table:
Claims (9)
1. the austenite TWIP type with high mechanical resistance and formability manufacturing high Mn content is (twin
Brilliant induced plasticity) method of steel, it is characterised in that described steel has following chemical composition, with
Percentage by weight meter:
C 0.2-1.5；Mn 10-25；Optionally Ni < 2；Si 0.05-2.00；Al 0.01-2.0；
0.01≤N<0.1；P+Sn+Sb+As<0.2；S+Se+Te<0.5；And Nb+Co 0.1-0.4 and/or
Re+W 0.2-0.7, in addition to inevitable impurity, remaining is Fe, heavily ties after the most cold rolling
Brilliant annealing, including:
Continuous annealing, is carried out within the temperature range of 900 DEG C-1100 DEG C, and time interval was at 60 seconds
Between 120 seconds；Or
Batch annealing, is carried out within the temperature range of 700 DEG C-800 DEG C, and time interval is at 30 points
Clock between 400 minutes,
Wherein annealing atmosphere has carbon activity a between 0.1 and 1.0c, and for continuous annealing,
Nitrogen content is between 90% and 100%, for batch annealing, nitrogen content between 0% and 100%,
For continuous annealing, hydrogen content is between 0% and 10%, and for batch annealing, hydrogen content exists
Between 0% and 100%, the dew point of continuous annealing and batch annealing is less than 0 DEG C.
2. the method for claim 1, it is characterised in that for single alloying element or alloy
The combination of element, compositing range independently of each other:
C 0.4-0.8；Mn 16-19；Optionally Ni < 1.0；Si 0.2-0.4；Al 0.1-1.5；N 0.01-0.05；
And Nb+Co 0.1-0.4 and/or Re+W 0.3-0.7.
3. method as claimed in claim 1 or 2, it is characterised in that described method includes preparation gold
Belonging to the further operation of coating, described metal coating passes through based on zinc containing magnesium and aluminum under heat condition
Alloy obtain.
4. the method for claim 1, it is characterised in that continuous annealing and the dew of batch annealing
Point is between-10 DEG C and-50 DEG C.
5. there is the austenitic steel of twin crystal induction plastic (TWIP), it is characterised in that described steel tool
There is following chemical composition, by weight percentage:
C 0.2-1.5；Mn 10-25；Optionally Ni < 2；Si 0.05-2.00；Al 0.01-2.0；
0.01≤N<0.1；P+Sn+Sb+As<0.2；S+Se+Te<0.5；And Nb+Co 0.1-0.4 and/or
Re+W 0.2-0.7, in addition to inevitable impurity, remaining is Fe, and can pass through claim 1 institute
The method stated obtains, and has a following mechanical property:
Rp0.2 between 250 and 350MPa
Rm between 850 and 1100MPa
A80 between 60% and 100%.
6. austenitic steel as claimed in claim 5, it is characterised in that there is consisting of: C
0.4-0.8；Mn 16-19；Optionally Ni < 1.0；Si 0.2-0.4；Al 0.1-1.5；N 0.01-0.05；
And Nb+Co 0.1-0.4 and/or Re+W 0.3-0.7, and can be by the side described in claim 2
Method obtains.
7. the austenitic steel as described in claim 5 or 6 is for manufacturing the purposes of complex geometry parts,
Described parts are used for absorbing energy, structure-reinforced and automobile application.
8. high Mn content steel, it is characterised in that there is following chemical composition, by weight percentage:
C 0.2-1.5；Mn 10-25；Optionally Ni < 2；Si 0.05-2.00；Al 0.01-2.0；0.01≤N<0.1；
P+Sn+Sb+As<0.2；S+Se+Te<0.5；And Nb+Co 0.1-0.4 and/or Re+W 0.2-0.7,
In addition to inevitable impurity, remaining is Fe.
9. steel as claimed in claim 8, it is characterised in that for single alloying element or alloy unit
The combination of element, compositing range is: C 0.4-0.8；Mn 16-19；Optionally Ni < 1.0；Si 0.2-0.4；
Al 0.1-1.5；N 0.01-0.05；And Nb+Co 0.1-0.4 and/or Re+W 0.3-0.7.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| ITRM2010A000641 | 2010-12-07 | ||
| ITRM2010A000641A IT1403129B1 (en) | 2010-12-07 | 2010-12-07 | PROCEDURE FOR THE PRODUCTION OF HIGH MANGANESE STEEL WITH MECHANICAL RESISTANCE AND HIGH FORMABILITY, AND STEEL SO OBTAINABLE. |
| PCT/IT2011/000401 WO2012077150A2 (en) | 2010-12-07 | 2011-12-07 | Process for manufacturing high manganese content steel with high mechanical resistance and formability, and steel so obtainable |
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| Publication Number | Publication Date |
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| CN103339279A CN103339279A (en) | 2013-10-02 |
| CN103339279B true CN103339279B (en) | 2016-09-28 |
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| Country | Link |
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| EP (1) | EP2649214B1 (en) |
| KR (1) | KR20140025324A (en) |
| CN (1) | CN103339279B (en) |
| IT (1) | IT1403129B1 (en) |
| WO (1) | WO2012077150A2 (en) |
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| DE102013003516A1 (en) | 2013-03-04 | 2014-09-04 | Outokumpu Nirosta Gmbh | Process for the production of an ultra-high-strength material with high elongation |
| KR101657808B1 (en) * | 2014-12-22 | 2016-09-20 | 주식회사 포스코 | Austenitic steel with excellent resistance for adiabatic shear band formability and method for manufacturing thereof |
| TWI504756B (en) | 2015-01-30 | 2015-10-21 | China Steel Corp | Manufacture method of high strength and high ductility steel |
| EP3095889A1 (en) | 2015-05-22 | 2016-11-23 | Outokumpu Oyj | Method for manufacturing a component made of austenitic steel |
| ES2673429T3 (en) | 2015-07-16 | 2018-06-21 | Outokumpu Oyj | Method for manufacturing a TWIP or TRIP / TWIP austenitic steel component |
| EP3173504A1 (en) | 2015-11-09 | 2017-05-31 | Outokumpu Oyj | Method for manufacturing an austenitic steel component and use of the component |
| EP3395979B1 (en) | 2015-12-24 | 2020-06-03 | Posco | Austenite-based molten aluminum-plated steel sheet having excellent properties of plating and weldability, and method for manufacturing same |
| CN105755388B (en) * | 2016-04-18 | 2018-04-24 | 和县隆盛精密机械有限公司 | A kind of casting method of mechanical arm high-strength abrasion-proof casting |
| DE102016117494A1 (en) * | 2016-09-16 | 2018-03-22 | Salzgitter Flachstahl Gmbh | Process for producing a formed component from a medium manganese steel flat product and such a component |
| KR101903174B1 (en) | 2016-12-13 | 2018-10-01 | 주식회사 포스코 | Low alloy steel sheet with excellent strength and ductility |
| KR20190138835A (en) | 2017-04-11 | 2019-12-16 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | Cold rolled flat steel product annealed in a bell furnace and its manufacturing method |
| CN107574377B (en) * | 2017-09-07 | 2019-05-03 | 北京科技大学 | A kind of high energy absorption type high manganese TWIP steel based on nanostructure and preparation method thereof |
| KR101952818B1 (en) | 2017-09-25 | 2019-02-28 | 주식회사포스코 | Low alloy steel sheet with high strength and ductility and method of manufacturing same |
| CN111771009A (en) * | 2018-01-05 | 2020-10-13 | 香港大学 | A kind of automobile steel and its manufacturing method |
| CN117265419A (en) * | 2022-06-15 | 2023-12-22 | 宝山钢铁股份有限公司 | High-formability, easy-phosphating and high-manganese cold-rolled steel sheet with strength of 1000-1600MPa and manufacturing method thereof |
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| US20080083477A1 (en) * | 2004-10-20 | 2008-04-10 | Arcelor France | Hot-Dip Coating Method in a Zinc Bath for Strips of Iron/Carbon/Manganese Steel |
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| FR2796083B1 (en) * | 1999-07-07 | 2001-08-31 | Usinor | PROCESS FOR MANUFACTURING IRON-CARBON-MANGANESE ALLOY STRIPS, AND STRIPS THUS PRODUCED |
| DE10259230B4 (en) * | 2002-12-17 | 2005-04-14 | Thyssenkrupp Stahl Ag | Method for producing a steel product |
| FR2876708B1 (en) * | 2004-10-20 | 2006-12-08 | Usinor Sa | PROCESS FOR MANUFACTURING COLD-ROLLED CARBON-MANGANESE AUSTENITIC STEEL TILES WITH HIGH CORROSION RESISTANT MECHANICAL CHARACTERISTICS AND SHEETS THUS PRODUCED |
| FR2878257B1 (en) * | 2004-11-24 | 2007-01-12 | Usinor Sa | PROCESS FOR MANUFACTURING AUSTENITIC STEEL SHEET, FER-CARBON-MANGANIZED WITH VERY HIGH RESISTANCE AND ELONGATION CHARACTERISTICS, AND EXCELLENT HOMOGENEITY |
| US20090165897A1 (en) * | 2005-02-02 | 2009-07-02 | Corus Staal Bv | Austenitic steel having high strength and formability, method of producing said steel and use thereof |
| EP1878811A1 (en) * | 2006-07-11 | 2008-01-16 | ARCELOR France | Process for manufacturing iron-carbon-manganese austenitic steel sheet with excellent resistance to delayed cracking, and sheet thus produced |
| KR100985286B1 (en) * | 2007-12-28 | 2010-10-04 | 주식회사 포스코 | High strength and high manganese steel excellent in delayed fracture resistance and manufacturing method |
| US8528379B2 (en) | 2009-04-08 | 2013-09-10 | Kirk Ernest Williamson | Method and apparatus for applying tension to flexible items |
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- 2010-12-07 IT ITRM2010A000641A patent/IT1403129B1/en active
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20080083477A1 (en) * | 2004-10-20 | 2008-04-10 | Arcelor France | Hot-Dip Coating Method in a Zinc Bath for Strips of Iron/Carbon/Manganese Steel |
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| Publication number | Publication date |
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| ITRM20100641A1 (en) | 2012-06-08 |
| IT1403129B1 (en) | 2013-10-04 |
| EP2649214B1 (en) | 2016-12-07 |
| WO2012077150A3 (en) | 2012-11-22 |
| KR20140025324A (en) | 2014-03-04 |
| CN103339279A (en) | 2013-10-02 |
| EP2649214A2 (en) | 2013-10-16 |
| WO2012077150A2 (en) | 2012-06-14 |
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