CN105755371B - Manganese low-temperature steel and preparation method thereof in a kind of high-strength low-yield ratio without nickel - Google Patents
Manganese low-temperature steel and preparation method thereof in a kind of high-strength low-yield ratio without nickel Download PDFInfo
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- CN105755371B CN105755371B CN201610197044.7A CN201610197044A CN105755371B CN 105755371 B CN105755371 B CN 105755371B CN 201610197044 A CN201610197044 A CN 201610197044A CN 105755371 B CN105755371 B CN 105755371B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
The present invention is manganese low-temperature steel in a kind of high-strength low-yield ratio without nickel, and its chemical composition and its mass fraction are：C：0.03‑0.06%、Mn：4.5‑6.0%、Si：0.15‑0.23%、Als：0.015 0.030%, Mo：0.1 0.3%, S≤0.006%, P≤0.009%, surplus is Fe and impurity element；The metallographic structure of the low-temperature steel is the heterogeneous structure of tempering ferrite lath beam+rotary austenite.The present invention makes material obtain superior low-temperature toughness, cost is substantially reduced compared with other low-temperature steels by the alloy design method and rational rolling and Technology for Heating Processing of substitute nickel with manganese.Meanwhile, low-temperature steel of the invention also has high-yield strength and the distinguishing feature of low yield strength ratio, thus application wider, safety of structure is higher.
Description
Technical field
The present invention relates to a kind of low-temperature steel and preparation method thereof, in specifically a kind of high-strength low-yield ratio without nickel
Manganese low-temperature steel and preparation method thereof.
Background technology
Low-temperature steel is the general designation for the steel for using and having enough notch toughnesses in a low temperature of less than -10 DEG C, and it develops
There is last 100 yearses history, effectively promoted the progress of low temperature field Science and Technology.Low-temperature steel is broadly divided into four classes, i.e. low-carbon
Aluminum killed steel, low-temperature high-strength steel, nickel system low-temperature steel and austenitic stainless steel.
Carbon aluminium-killed steel is the low-temperature steel using C, Mn as essential element, by reducing C content, improving Mn/C ratios, reduction
The harmful elements such as S, P and add and appropriate can fix the Al of N and crystal grain thinning and improve the mesh of material at low temperature toughness to reach
's.By taking 16MnDR, 15MnNiDR and 09MnNiDR as an example, the C content of these low-temperature steels is controlled below 0.2%, Mn content controls
Scope processed is 1.2-1.6%, and Als contents are controlled more than 0.015%, also added Ni in most cases in addition；From power
Learn from the point of view of performance, the yield strength of these low-temperature steels is relatively low, about 300MPa, Charpy-type test temperature is -30 DEG C to -70
℃。
Low-temperature high-strength steel is based on C, Mn, to add a small amount of Ni and Cr to improve low-temperature flexibility, and add on a small quantity
Mo and V improves intensity, and obdurability matching is preferable, be mainly used in the spherical tank in Cryo Equipment.For example China is in 1985-1990
Between the DG50 that develops, this steel carbon content control is in 0.09-0.15%, and the control of Mn contents is at 1.0-1.4%, Ni, Cr, Mo and V points
Do not control 0.6%, 0.3%, 0.3% and less than 0.06%；Its yield strength in more than 490MPa, Charpy-type test temperature for-
46℃。
Ductil-brittle transition temperature is greatly lowered by the Ni of high level using Ni as main alloy element in nickel system low-temperature steel.
According to the difference of temperature in use, the Ni contents of this kind of low-temperature steel can be 1.5%, 3.5%, 5% and 9%, Charpy-type test temperature
Respectively -80 DEG C, -110 DEG C, -120 DEG C and -196 DEG C, yield strength be respectively higher than 275MPa, 345MPa, 390MPa and
575MPa.The 9Ni steel of the mass fraction of element containing Ni 9%, its typical organization is tempered martensite+rotary austenite, tempered martensite
Matrix provides higher intensity, and rotary austenite is as the absorber of deformation load, can hinder the germinating of deformation crackle with
Extension, so as to improve low-temperature flexibility.
Austenitic stainless steel mainly includes chromium nickel stainless steel and chromium manganese nickel nitrogen stainless steel, containing substantial amounts of Cr, Ni and Mn, with
Stable austenite phase is matrix, no ductil-brittle transition phenomenon, excellent in low temperature toughness, such as 304L, 304LN and 316L
Temperature in use can reach -196 DEG C.
For current existing low-temperature steel, Ni is most basic most important alloying element, and the element can form α with Fe
Or γ solid solution, it can also improve tough by the approach of stable austenite phase while the matching of ferritic phase obdurability is improved
Property, ductil-brittle transition temperature is significantly reduced, but Ni a large amount of additions improve material cost.Have as another of low-temperature steel
Beneficial element, Mn can reduce ductil-brittle transition temperature and improve low-temperature flexibility, and price advantage is obvious compared with Ni.If can
Ni partially or completely is replaced with appropriate Mn, then can substantially reduce the cost of alloy of low-temperature steel, improve the warp of low-temperature steel
Ji property.In addition, application can undoubtedly be expanded by improving the yield strength of low-temperature steel, but if using steel if sacrificing yield tensile ratio as cost
The security of structure is difficult to ensure that.Regrettably, current low-temperature steel be difficult to and meanwhile meet section nickel drop this, high intensity and low bend strong
Compare the characteristics of.
The content of the invention
The technical problems to be solved by the invention are the shortcomings for overcoming prior art, are proposed a kind of low without nickel element
Wen Gang, its yield strength is high and yield tensile ratio is low, has excellent in toughness in -110 DEG C of low temperature environments.
Another technical problem to be solved by this invention is to propose the preparation method of above-mentioned low-temperature steel
The present invention solve above technical problem technical scheme be：
Manganese low-temperature steel in a kind of high-strength low-yield ratio without nickel, its chemical composition and its mass fraction are：C：0.03-
0.06%、Mn：4.5-6.0%、Si：0.15-0.23%、Als：0.015-0.030%, Mo：0.1-0.3%, S≤0.006%, P≤
0.009%, surplus is Fe and impurity element；The metallographic structure of the low-temperature steel is tempering ferrite lath beam+rotary austenite
Heterogeneous structure.
The preparation method of manganese low-temperature steel, comprises the following steps in high-strength low-yield ratio without nickel：
(i) heat：By the blank heating with chemical composition identical with the low-temperature steel to 1050-1150 DEG C, and it is incubated
90-180min；
(ii) roll：Two-phase control rolling, 930-1050 DEG C of a stage rolling temperature, passage deformation are carried out to the blank after heating
Amount >=15%, 780-870 DEG C of two-stage rolling temperature, total deformation >=50%, rolling is air-cooled to room temperature after terminating；
(iii) it is heat-treated：Steel plate is heated to 800-860 DEG C, and is incubated 30-50min, then with the cooldown rate more than 5 DEG C/s
Acceleration, which is cooled to after 390-460 DEG C, is air-cooled to room temperature, and steel plate is heated into 625-665 DEG C afterwards and 20-60min is incubated, then empty
It is cooled to room temperature.
The technical scheme that further limits of the present invention is：
Manganese low-temperature steel in the foregoing high-strength low-yield ratio without nickel, the thickness for the sheet material being made up of the low-temperature steel is
17-60mm, yield strength >=600MPa, yield tensile ratio≤0.85, elongation percentage >=32%, -110 DEG C of Charpy-type test side knocks
Absorb energy >=120J.
The restriction reason of chemical composition content is as follows in the present invention：
C element can improve intensity by solution strengthening or precipitation strength, at the same can stable austenite phase, but in order to drop
Low material ductil-brittle transition temperature, C content should be reduced as far as possible.In addition, C is also unfavorable for the weldability of material.Therefore the present invention will
C content controls the reduced levels in 0.03-0.06%.
Mn is the main alloy element of low-temperature steel of the present invention.Mn is ferritizing strengthening element, while being also austenite
Stable element.In terms of material at low temperature toughness is improved, ductil-brittle transition temperature, therefore Mn energy can be significantly reduced by improving Mn/C ratios
The higher Ni of enough prices of substitution to a certain extent.The purpose that Mn contents of the present invention are limited is：In order to without Ni elements
Under conditions of material is possessed superior low-temperature toughness, Mn additions is higher than low-alloy steel content range, but too high Mn contents
It will aggravate degree of segregation, difficulty increasing be smelted and material cost raising, by the control of Mn contents in 4.5-6.0%.
Si is deoxidant element in steelmaking process, and appropriate Si can suppress Mn and P segregation, and O content is too high, Mn and P
Segregation can all damage low-temperature flexibility.Si can also produce solution strengthening, but content more than 0.3% when can cause ductil-brittle transition temperature
Rise, therefore content can not be too high.The present invention is by Si controls in 0.15-0.23%.
Al in steelmaking process be deoxidant element, can also reduce solid solution N atomic quantities, thus improve toughness and when effect
Become drag, formed by AlN can also crystal grain thinning so that further reduce ductil-brittle transition temperature.But being excessively added to form
Large-sized Al3O2 and AlN simultaneously damage low-temperature flexibility.The present invention is by Al content（Als）Control is in 0.015-0.030%.
Mo can suppress cementite precipitation, additionally it is possible to improve temper resistance, so that reduce fragility and improve intensity, content
It is too high to increase material cost.The present invention is by the control of Mo contents in 0.1-0.3%.
S easily easily in Grain Boundary Segregation and reduces crystal boundary resistance to crack extension ability with Mn formation MnS, P, to improve material at low temperature
Toughness is, it is necessary to by S, P control in bottom line.
The mechanism of preparation method is as follows in the present invention：
The high temperature austenite tissue of certain crystallite dimension is obtained during blank heating, while alloying element is equal by diffusion way
Homogenize.Heating-up temperature is too high or soaking time is long that high temperature austenite crystal grain will be caused excessively thick, and heating-up temperature it is too low or
The too short homogenization for being unfavorable for alloying elements distribution of soaking time, thus the present invention by heating and temperature control at 1050-1150 DEG C,
Soaking time is controlled in 90-180min.Blank carries out two-phase control rolling after heating, and a stage rolling temperature is controlled in 930-1050
DEG C, in austenite perfect recrystallization area, pass deformation >=15% can reach preferable recrystallization softening effect；Two-stage
Rolling temperature is controlled at 780-870 DEG C, and in austenite Unhydrated cement, total deformation >=50% ensure that enough strains
Accumulate and refine the phase-change organization after cooling, favourable forerunner's tissue is provided for heat treatment.First steel plate is heated during heat treatment
To 800-860 DEG C, the temperature range is located at austenite phase field, and 30-50min soaking time can then make austenitizing completely,
Make alloying elements distribution uniform enough simultaneously, temperature is too high or soaking time is long can cause coarse grains and reduce toughness.It is difficult to understand
Cooling is accelerated with >=5 DEG C/s cooldown rate in high temperature section after the insulation of family name's bodyization, because material Mn contents are high, thus quenching degree
Height, accelerates cooling to suppress the high temperature of overcooling austenite and middle temperature phase transformation, accelerates cooling to suppress thick carbonization in addition
The formation of thing, is conducive to improving low-temperature flexibility.The final cooling temperature of cooling is accelerated to select at 390-460 DEG C, the temperature range compares
Approach but still higher than Cooling Austenite Transformation critical point, in the process air cooler after, phase transformation is slower and uniform
Progressively carried out during temperature drop, the ferrite lath beam plus size refined be tiny and retained austenite of Dispersed precipitate or M-
A constituent elements, favourable forerunner's tissue is provided to obtain the rotary austenite of perfect condition in next step Technology for Heating Processing.In addition,
The above-mentioned type of cooling stage by stage is taken to be also beneficial to alleviate steel plate internal stress and prevent crackle.In second step Technology for Heating Processing
In, steel plate is heated to 625-665 DEG C, the temperature range is in austenite-ferrite two-phase section, insulating process and can formed
Certain volume fraction（5-12%）Rotary austenite, rotary austenite is rich in temperature-rise period and 20-60min insulating process
Collect alloying element to obtain enough heat endurances, face-centred cubic structure can be remained in that at a temperature of -110 DEG C, and iron is plain
Appropriate reply occurs at high temperature for body lath beam, and matrix mechanical property is improved.Room temperature is air-cooled to after insulation to be tempered
Ferrite lath beam adds the heterogeneous structure of rotary austenite, is matched with excellent obdurability, particularly with excellent low temperature
Toughness.In addition, a part of rotary austenite can material occur strain phase be changed into martensite, thus improve tensile strength,
Yield tensile ratio is reduced, the plastic deformation ability of material is optimized.
The beneficial effects of the invention are as follows：
The present invention obtains material by the alloy design method and rational rolling and Technology for Heating Processing of substitute nickel with manganese
Superior low-temperature toughness, cost is substantially reduced compared with other low-temperature steels.Meanwhile, low-temperature steel of the invention also has high-yield strength
With the distinguishing feature of low yield strength ratio, thus application is wider, safety of structure is higher.
The low-temperature steel of the present invention and low-temperature impact test temperature requirement identical 3.5Ni steel（A kind of nickel system low-temperature steel）Phase
Than the cost of alloy of low-temperature steel proposed by the present invention reduces about 1500 yuan/ton, and has concurrently while yield strength is higher low
The characteristics of yield tensile ratio, application is wider.
Compared with prior art, patent CN104911475A discloses manganese high-strength tenacity special heavy plate in a kind of low-carbon to the present invention
And preparation method thereof, in chemical composition C content higher than the present invention, the press quenching taken in technique different from the present invention add from
Line is tempered, and steel plate thickness is beyond the scope of the invention, and elongation percentage is less than the present invention in plate property and only ensures more than -60 DEG C low
Warm toughness；Patent CN104946973A discloses manganese cut deal and its preparation side in the low-carbon of high intensity, toughness, plasticity a kind of
Method, the significant difference with the present invention is to the addition of Ni elements in chemical composition, and aspect of performance only ensures more than -80 DEG C low temperature in addition
Toughness.
Brief description of the drawings
Fig. 1 is low-temperature steel metallographic structure figure in embodiment 1.
Fig. 2 is low-temperature steel metallographic structure figure in embodiment 2.
Fig. 3 is low-temperature steel metallographic structure figure in embodiment 3.
Embodiment
Embodiment 1
The present embodiment 1 is manganese low-temperature steel sheet material in the high-strength low-yield ratio without nickel that thickness is 60mm, chemical composition and
Its mass fraction is respectively 0.04%C, 5.1%Mn, 0.23%Si, 0.02%Als, 0.16%Mo, 0.006%S, 0.007%P, Yi Jiyu
Fe and impurity element are measured, metallographic structure is the heterogeneous structure of tempering ferrite lath beam+rotary austenite, yield strength
609MPa, yield tensile ratio 0.78, elongation percentage 37%, it is 152J that -110 DEG C of Charpy-type test side knocks, which absorb energy,.
The preparation technology of above-mentioned low-temperature steel sheet material is followed the steps below：
The thick blanks of 320mm are put into heating furnace and is heated to 1050 DEG C and is incubated 180min, the chemical composition of blank and
Its mass fraction is respectively 0.04%C, 5.1%Mn, 0.22%Si, 0.02%Als, 0.16%Mo, 0.006%S, 0.007%P, Yi Jiyu
Measure Fe and impurity element；
Two-phase control rolling, 1005 DEG C of a stage start rolling temperature, 930 DEG C of finishing temperature, milling train are carried out to the blank after heating
Rolling schedule is 320mm -240mm -180mm -138mm；870 DEG C of two-stage start rolling temperature, 820 DEG C of finishing temperature, milling train pressure
Lower code is 138mm -110mm -88mm- 72mm -60mm, and rolling terminates cold bed on rear steel plate and is air-cooled to room temperature；
Steel plate is put into heating furnace and is heated to 825 DEG C and is incubated 60min, water cooling is to 440 DEG C, Zhi Houkong after steel plate is come out of the stove
It is cooled to room temperature, then steel plate is put into heating furnace is heated to 650 DEG C and is incubated 60min, steel plate is air-cooled to room temperature after coming out of the stove.
Fig. 1 is the present embodiment low-temperature steel metallographic structure figure, and organization type is tempering ferrite lath beam+rotary austenite
Heterogeneous structure.
Embodiment 2
The present embodiment thickness is manganese low-temperature steel sheet material, chemical composition and its matter in the 41mm high-strength low-yield ratio without nickel
It is respectively 0.06%C, 4.5%Mn, 0.15%Si, 0.03%Als, 0.3%Mo, 0.001%S, 0.009%P, and surplus Fe to measure fraction
And impurity element, metallographic structure is the heterogeneous structure of tempering ferrite lath beam+rotary austenite, and yield strength 637MPa is bent
Strong to compare 0.82, elongation percentage 35%, -110 DEG C of Charpy-type test side knocks absorb energy for 131J.
The preparation technology of above-mentioned low-temperature steel sheet material is followed the steps below：
The thick blanks of 280mm are put into heating furnace and is heated to 1120 DEG C and is incubated 120min, the chemical composition of blank and
Its mass fraction is respectively 0.06%C, 4.5%Mn, 0.15%Si, 0.03%Als, 0.3%Mo, 0.001%S, 0.009%P, Yi Jiyu
Measure Fe and impurity element；
Two-phase control rolling, 1020 DEG C of a stage start rolling temperature, 960 DEG C of finishing temperature, milling train are carried out to the blank after heating
Rolling schedule is 280mm -196mm -147mm -105mm；860 DEG C of two-stage start rolling temperature, 805 DEG C of finishing temperature, milling train pressure
Lower code is 105mm -84mm -66mm- 53mm -45mm -41mm, and rolling terminates cold bed on rear steel plate and is air-cooled to room temperature；
Steel plate is put into heating furnace and is heated to 860 DEG C and is incubated 30min, water cooling is to 460 DEG C, Zhi Houkong after steel plate is come out of the stove
It is cooled to room temperature, then steel plate is put into heating furnace is heated to 665 DEG C and is incubated 35min, steel plate is air-cooled to room temperature after coming out of the stove.
Fig. 2 is the present embodiment low-temperature steel metallographic structure figure, and organization type is tempering ferrite lath beam+rotary austenite
Heterogeneous structure.
Embodiment 3
The present embodiment is manganese low-temperature steel sheet material in the high-strength low-yield ratio without nickel that thickness is 17mm, chemical composition and its
Mass fraction is respectively 0.03%C, 6.0%Mn, 0.20%Si, 0.015%Als, 0.1%Mo, 0.003%S, 0.006%P, and surplus
Fe and impurity element, metallographic structure is the heterogeneous structure of tempering ferrite lath beam+rotary austenite, yield strength 654MPa,
Yield tensile ratio 0.85, elongation percentage 32%, it is 120J that -110 DEG C of Charpy-type test side knocks, which absorb energy,.
The preparation technology of above-mentioned low-temperature steel sheet material is followed the steps below：
The thick blanks of 180mm are put into heating furnace and is heated to 1150 DEG C and is incubated 90min, the chemical composition of blank and its
Mass fraction is respectively 0.03%C, 6.0%Mn, 0.20%Si, 0.015%Als, 0.1%Mo, 0.003%S, 0.006%P, and surplus
Fe and impurity element；
Two-phase control rolling, 1050 DEG C of a stage start rolling temperature, 955 DEG C of finishing temperature, milling train are carried out to the blank after heating
Rolling schedule is 180mm -126mm -88mm -69mm -55mm；855 DEG C of two-stage start rolling temperature, 780 DEG C of finishing temperature, roll
Machine rolling schedule is 55mm -44mm- 35mm -28mm -23mm -19mm -17mm, and rolling terminates cold bed air cooling on rear steel plate
To room temperature；
Steel plate is put into heating furnace and is heated to 800 DEG C and is incubated 50min, water cooling is to 390 DEG C, Zhi Houkong after steel plate is come out of the stove
It is cooled to room temperature, then steel plate is put into heating furnace is heated to 625 DEG C and is incubated 20min, steel plate is air-cooled to room temperature after coming out of the stove.
Fig. 3 is the present embodiment low-temperature steel metallographic structure figure, and organization type is tempering ferrite lath beam+rotary austenite
Heterogeneous structure.
In addition to the implementation, the present invention can also have other embodiment.All use equivalent substitution or equivalent transformation shape
Into technical scheme, all fall within the protection domain of application claims.
Claims (7)
1. the preparation method of manganese low-temperature steel in a kind of high-strength low-yield ratio without nickel, its chemical composition and its mass fraction are：
C：0.03-0.06%、Mn：4.5-6.0%、Si：0.15-0.23%、Als：0.015-0.030%, Mo：0.1-0.3%, S≤
0.006%, P≤0.009%, surplus is Fe and impurity element；The metallographic structure of the low-temperature steel is tempering ferrite lath beam+return
Turn the heterogeneous structure of austenite；It is characterized in that：The preparation method comprises the following steps：
(i) heat：By the blank heating with chemical composition identical with the low-temperature steel to 1050-1150 DEG C, and it is incubated 90-
180min；
(ii) roll：To after heating blank carry out two-phase control rolling, 930-1050 DEG C of a stage rolling temperature, pass deformation >=
15%, 780-870 DEG C of two-stage rolling temperature, total deformation >=50%, rolling is air-cooled to room temperature after terminating；
(iii) it is heat-treated：Steel plate is heated to 800-860 DEG C, and is incubated 30-50min, then is accelerated with the cooldown rate more than 5 DEG C/s
It is cooled to after 390-460 DEG C and is air-cooled to room temperature, steel plate is heated to 625-665 DEG C afterwards and 20-60min is incubated, then is air-cooled to
Room temperature.
2. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：By
The thickness for the sheet material that the low-temperature steel is made be 17-60mm, yield strength >=600MPa, yield tensile ratio≤0.85, elongation percentage >=
32%, -110 DEG C of Charpy-type test side knocks absorb energy >=120J.
3. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：Base
Material is heated to 1050-1150 DEG C, and is incubated 90-180min, the high temperature austenite tissue of certain crystallite dimension is obtained, while alloy
Element is homogenized by diffusion way.
4. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：Plus
Blank carries out two-phase control rolling after heat, and a stage rolling temperature is controlled at 930-1050 DEG C, in austenite perfect recrystallization area,
Pass deformation >=15%, reaches recrystallization softening effect；Two-stage rolling temperature is controlled at 780-870 DEG C, in austenite not
Recrystallization zone, total deformation >=50%, it is ensured that enough strain accumulation simultaneously refines the phase-change organization after cooling, is provided for heat treatment
Favourable forerunner's tissue.
5. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：Heat
Steel plate is first heated to 800-860 DEG C during processing, 30-50min is incubated, makes austenitizing completely, while making alloying elements distribution
It is uniform enough；Cooling is accelerated with >=5 DEG C/s cooldown rate in high temperature section after austenitizing insulation, suppresses the height of overcooling austenite
Warm and middle temperature phase transformation, while suppressing the formation of thick carbide, is conducive to improving low-temperature flexibility.
6. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：With
Cooldown rate more than 5 DEG C/s accelerates to be cooled to after 390-460 DEG C the ferrite lath beam plus chi for being air-cooled to room temperature, being refined
Very little tiny and Dispersed precipitate retained austenite or M-A constituent elements, are the revolution that perfect condition is obtained in next step Technology for Heating Processing
Austenite provides favourable forerunner and organized.
7. the preparation method of manganese low-temperature steel in the high-strength low-yield ratio as claimed in claim 1 without nickel, it is characterised in that：Will
Steel plate is heated to 625-665 DEG C, forms volume fraction 5-12% rotary austenite, rotary austenite is in temperature-rise period and 20-
Alloying element is enriched with 60min insulating process to obtain enough heat endurances, can be remained in that at a temperature of -110 DEG C
Face-centred cubic structure, and appropriate reply occurs at high temperature for ferrite lath beam, matrix mechanical property is improved；It is empty after insulation
It is cooled to room temperature to obtain being tempered ferrite lath beam plus the heterogeneous structure of rotary austenite, a part of rotary austenite can be in material
Generation strain phase is changed into martensite.
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| CN104805378A (en) * | 2015-05-13 | 2015-07-29 | 东北大学 | High strength and toughness ultra-low carbon medium manganese steel middle-thickness plate and preparation method thereof |
| CN104911475A (en) * | 2015-06-25 | 2015-09-16 | 东北大学 | Low-carbon medium-manganese high-toughness super-thick steel plate and preparation method thereof |
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| CN104805378A (en) * | 2015-05-13 | 2015-07-29 | 东北大学 | High strength and toughness ultra-low carbon medium manganese steel middle-thickness plate and preparation method thereof |
| CN104911475A (en) * | 2015-06-25 | 2015-09-16 | 东北大学 | Low-carbon medium-manganese high-toughness super-thick steel plate and preparation method thereof |
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