CN106350739A - High-strain-rate medium-low carbon medium-low alloy super-plastic steel and preparation method - Google Patents
High-strain-rate medium-low carbon medium-low alloy super-plastic steel and preparation method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- 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
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- 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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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
The invention provides high-strain-rate medium-low carbon medium-low alloy super-plastic steel and a preparation method, and belongs to the technical field of high-strength and super-plastic steel and super-plastic forming. The high-strain-rate medium-low carbon medium-low alloy super-plastic steel comprises the following chemical components in percentages by weight: 0.01-0.49% of C, 2.5-13.0% of Mn, 0-12.0% of Al, 0-3.0% of Si, 0-3.0% of Cr, 0-3.0% of Ni and the balance of Fe and inevitable impurities. On the basis, the following one or more elements can be added: 0-0.2% of Mo, 0-0.20% of Nb, 0-0.20% of Ti, 0-0.20% of V and 0-0.20% of Re. The medium-low carbon low-alloy hot-rolled and cold-rolled super-plastic steel with super-plasticity is produced by traditional processes such as smelting, casting, hot-rolling, heat treatment and cold-rolling, and has the advantages of excellent 100-1,500% of super-plasticity and 700-1,500 MPa of tensile strength at room temperature after super-plasticity deformation.
Description
Technical field
The invention belongs to high strength steel superplasticity steel and Superplastic Forming Techniques field, in particular, provide a kind of series
Change low-alloy superplasticity steel and preparation method in low-carbon (LC) in high strain rate.
Technical background
Plasticity refers under given conditions, that is, in low strain rate (ε=10-2～10-4s-1), certain deformation temperature
The degree half of thermodynamics fusion temperature (about) and stably and under conditions of tiny grain size (0.5～5 μm), some metals or
Alloy assumes low-intensity and a kind of characteristic of the percentage elongation more than 100%.The earliest report of Superplasticity Phenomenon is in nineteen twenty,
Rosenhain etc. finds that zn-4cu-7al alloy, when low speed bends, can bend nearly 180 °.1934, c.p.pearson sent out
Existing pb-sn eutectic alloy can obtain 2000% elongation percentage in room temperature low-speed tensile.A.a.bochvar in 1945 etc. finds
Zn-al eutectoid alloy has abnormal high elongation percentage and proposes " superplasticity " this noun.1964, w.a.backofen pair
Zn-al alloy has carried out systematic research, and proposes this new ideas of strain rate sensitivity m, is that superplasticity is ground
Study carefully and lay a good foundation.
20 century 70s play people and note developing the superplasticity of industrial trade mark alloy, are based on above-mentioned organization condition, super
Material will be carried out before plastic deformation or shaping with the pretreatment of crystal grain thinning, including heat treatment and thermomechanical treatment, some process
Technique is quite numerous and diverse, consumes the energy, manpower and material.Find under study for action many industrial alloys under supply of material state part although
The organization condition of uniform isometry fine grain can not be fully met, but (ti-6al-4v is exactly therein also to have good superplasticity
One typical case).So use no or little micronization processes technique, the economy of plastic technology can have been greatly improved.Therefore supply
The research and development of state superplastic alloy have become superplastic material and an important R＆D direction of superplastic forming research and development.
Up to the present it has been found that numerous aluminum and aluminium alloy, magnesium and magnesium alloy, titanium or titanium alloy and other metal
There is superplasticity, but be difficult to realize superplasticforming in middle low-carbon low-alloy steel field.The seventies in last century, American scientist
O.d.sherby etc. has started with the superplastic research work of the superhigh carbon steel of 1.0-2.1%c, finds superhigh carbon steel and applies for
A series of have superplastic superhigh carbon steel patent, opens the research superplastic basic research of ferrous materials and applied research work
Make.In addition in heavy alloyed rustless steel field (austenitic stainless steel and two phase stainless steel, the precious alloy such as its ni, cr, mn, mo
Content has reached 30% about), people are it has also been found that within the temperature range of 900-1200 DEG C, it is possible to obtain 100-2500%'s is super
Plasticity.In view of the shortcomings of poor and stainless alloy content of the solderability of superhigh carbon steel is high, exploring low-carbon (LC) in exploitation always low
The superplasticity of steel alloy and its industrialization.But up to the present, the superplastic research of middle low carbon steel shows, existing middle low-carbon (LC) is low
Steel alloy is difficult to realize superplasticity, more do not develop without heat treatment and thermomechanical treatment can heavy industrialization the supply of material
The superplasticity low medium carbon steel iron material of state.
The present invention proposes, by being designed to alloying component and traditional rolling (hot rolling and cold rolling), to obtain a kind of hot rolling
Or cold rolling the supply of material the superplastic middle low-carbon (LC) sheet material of state, in 550-1200 DEG C of high temperature warm area and the deformation in the 0.1-0.001/ second
The superplastic hot rolling of middle low-carbon (LC) of 200%-1500% elongation percentage and cold rolling steel are obtained under speed.Steel of the present invention has 0.01-
The middle low carbon content of 0.49%c, the steel plate after superplasticforming or parts have good welding performance and have after shaping
The room temperature tensile intensity of 700-1500mpa.This superplasticity steel plate by conventional smelting, continuous casting, hot rolling and cold rolling can be carried out
, it is not necessary to the heat treatment of complexity before superplastic deformation, becoming one kind can be with large-scale industry metaplasia for large-scale industrial production
The low middle carbon and low-alloy superplasticity steel of the supply of material state produced, has broken middle low-carbon low-alloy steel and has not had superplastic limitation, be super
Complex partses steel formability provides the superplastic material basis of industrialization supply of material state.
Content of the invention
It is an object of the invention to provide low-alloy superplasticity steel and preparation in low-carbon (LC) in a kind of seriation high strain rate
Method, is main adding elements and the microalloy element with the precipitation of the strong carbides such as ti, zr, nb, v and rare earth by mn, al and c
Alloying Design；Produce and there is superplastic ability by traditional smelting, casting, hot rolling, heat treatment and the operation such as cold rolling
The hot rolling of middle low-carbon and low-alloy and cold rolling superplasticity steel.
In 550-1250 DEG C of temperature and acquisition 100%-1500% extension in the range of the rate of deformation of 0.1-0.001/ second
Cold rolling steel of superplasticity of rate and preparation method thereof.Super High Carbon superplasticity steel with respect to traditional 1.0-2.1%c, steel of the present invention
There is the middle low carbon content of 0.01-0.49%c, by smelting, hot rolling and the cold rolling rolled obtaining there is superplasticity property and
The supply of material state sheet material of cold rolling state, can realize High-strength plate and the near-net-shape of other complex partses by superplastic forming.
Steel plate after superplasticforming or parts have good welding performance and the room temperature tensile intensity of 700-1500mpa.This surpasses
Plastic steel plate low-cost and easy-to produces, can by conventional smelting, continuous casting, hot rolling and cold rolling carry out large-scale industrial production,
Compensate for conventional ultra high carbon superplasticity steel non-welding character can and traditional low medium carbon steel the supply of material state under do not have superplastic
Defect is complex partses steel formability, reduce welding and lightweight provides material foundation.
The chemical component weight percent of the present invention is: c:0.01-0.49%, mn:2.5-13.0%, al:0-12.0%,
Si:0-3.0%, cr:0-3.0%, ni:0-3.0%, balance of fe and inevitable impurity；On this basis also can be another
Lower one kind or multiple element: mo:0-0.2%, nb:0-0.20%, ti:0-0.20%, v:0-0.20%, re:0-
0.20%.
This component system can ensure that having ultra-fine ferrite during superplasticforming is organized with austenitic duplex,
And ferrite is less than 5 microns with the crystallite dimension of austenite；Precipitation by microalloy elements such as ti, mo, nb, v and rare earths
Anchoring inhibiting grain growth, by ferrite, the crystallite dimension under the conditions of superplasticity controls to being less than with austenite further
2 microns, thus giving full play to the superplasticity ability of design steel.2nd, in superplastic deformation technique, mainly become at 550-1200 DEG C
Shape, in superplastic deformation process crystallite dimension in the range of 0.2-5 micron, to ensure the high temperature elongation percentage of superelevation and deformation no
Hole produces.3., in performance, steel of the present invention has the superplasticity property of excellent 100-1500% and the super of 700-1500mpa
Room temperature tensile strength after plastic deformation.
The effect of each element of the present invention and proportioning are according to as follows:
C: as main gap solution strengthening element, the ferrite during Superplastic Deformation and austenite content are entered
Row adjusts the intensity it is ensured that after superplastic duplex structure and shaping.But consideration welding requirements, c content should control no more than
In the range of 0.49wt%.
Mn:mn is austenite stabilizer element, and in the deformation process of high-temperature region, mn ensures high temperature austenite and duplex structure
Crystal grain tiny.Should control in the range of 2.50-13.00% for this mn content.
Al: al is the formation element promoting high temperature austenite and ferrite dual phase tissue in the present invention, can adjust heat
Ferrite in deformed microstructure and the content of austenite.Consider that al is element and the resistance to surface oxidation unit reducing steel density simultaneously
Element, can be greatly reduced the density of steel and improve the resistance to surface developmental capacity in superplastic deformation process.But too high al content
To the material cost being unfavorable for industrialized production and improve middle low carbon steel, therefore al content should control the scope in 0-12.0%
Interior.
Si: si is also to promote metastable austenite and ferrite dual phase to organize the formation of element in the present invention, can adjust heat
Ferrite in deformed microstructure and the content of austenite.Si can improve the intensity of steel by solid solution simultaneously.But the si more than 3%
Content can bring the problem of smelting, continuous casting and hot rolling.Therefore si content should control in the range of 0-3.0%.
Cr: promote high temperature austenite and ferrite dual phase to organize the formation of element, the ferrum element in thermal deformation tissue can be adjusted
Body and the content of austenite.The high temperature resistance surface oxidation ability of steel can be effectively improved simultaneously.But the one-tenth in view of low medium carbon steel
This, cr content controls in 0-3.0wt%.
Ni:ni and mn has same effect, can adjust under hot conditionss austenite and ferritic volume fraction and
Inhibiting grain growth, can effectively improve the toughness of the material after superplasticforming and parts.But the price of ni metal is high, its
Content should control below 3.0%.
Mo, nb, ti and v: be all the micro alloying element that strong carbide is formed, can suppress during superplasticforming
Crystal grain is grown up.Meanwhile, add the anti-hydrogen embrittlement sensitivity that these carbides can improve material after superplasticforming
Energy.But consider cost, these constituent contents control in the range of 0-0.2wt%.
The technical parameter of the manufacturing process of the present invention and control is:
The production technology of steel of the present invention is smeltings, casting, hot rolling, annealing and the process for making such as cold rolling, control in technique
The technical parameter of system is as follows:
(1) smelting of steel and solidification: be applied to converter, electric furnace and induction furnace and smelt, using continuous casting strand or molding
Produce ingot casting.
(2) hot rolling of strand or ingot casting or hot continuous rolling or forging:
Hot continuous rolling sheet material: strand is heated through 1100-1250 DEG C, finish rolling after first roughing, after rolling in the range of 300-700 DEG C
Carry out coiling into coil of strip, the superplasticity hot-strip of industrialization supply of material state can be obtained.
(3) soft annealing with cold rolling
Steel after thermal deformation are carried out in the range of 550-850 DEG C with soft annealing process to reduce steel plate hardness.Move back
The different drafts carrying out 0-90% after fire are cold rolling, can obtain the cold rolling steel of superplasticity of industrialization supply of material state.
(4) the reverse transformation annealing of cold rolled sheet
Steel after cold roller and deformed are made annealing treatment to obtain the room temperature of 20-50% in the range of 550-750 DEG C
High-ductility, can obtain the cold rolled annealed steel of superplasticity of industrialization supply of material state.
Brief description
Fig. 1 be 5# sample superplastic tension sample before being deformed after change in size figure.
Fig. 2 is the superplastic tension curve chart of 6# steel.
Fig. 3 is the variation diagram of specimen size before and after 6# steel superplastic tension.
Specific embodiment
Embodiment:
The present embodiment carries out, mainly for after strand hot rolling, reverse transformation annealing, the steel that hot warm-rolling obtains high-strength high-plasticity
Plate.Process of the test simulates the hot continuous rolling of steel plate, reverse transformation annealing and hot warm-rolling technique (partly hot warm-rolling after annealing).But this technique
It is equally applicable to the production of section bar and Bar Wire Product.
The smelting of steel:
Steel of the present invention, by test chamber vacuum induction furnace smelting, pours the billet that ingot mould is 50kg.Smelt 10 stove steel altogether, wherein
Chemical composition is shown in Table 1.Wherein 1-10 stove steel is invention steel, and cp steel, dp steel and ph steel are then smelted for simulation conventional multiphase steel
Low medium carbon steel compared steel.
Table 1 invention steel and the chemical composition (wt%) of compared steel
It is as follows that steel of the present invention implements example for technological process:
Step 1: the smelting of steel
By test chamber vacuum induction furnace smelting, pour the billet that ingot mould is 50kg.
Step 2: the forging of steel and hot rolling:
The steel ingot of 1-10# steel heats through 1250 DEG C, is incubated 5h, carries out hammer cogging.Just forging temperature is 1200 DEG C, eventually
Forging temperature is 800 DEG C, air cooling after forging.Finally it is forged into the blank of a size of 30mm × 100mm × 150mm.By above-mentioned forging base
Material heats through 1200 DEG C, after insulation 5h, passes through 7 passes by test hot-rolling mill, final steel board finished product thickness is 6mm.Rolling
Process simulation hot continuous rolling industrial processes, obtain the superplasticity steel plate with rolled.
Step 3: the soft annealing of hot-rolled steel:
1-10# steel is made annealing treatment at 650 DEG C, is incubated 6 hours, be not higher than 350hb just to reduce hot rolled plate hardness
In cold rolling.
Step 4: steel cold rolling:
The steel that step 3 is obtained carries out cold rolling, is rolled down to 70% deformation quantity.Obtain that there is superplastic cold rolling low middle carbon
Superplasticity steel.
Step 5: the reverse transformation annealing of cold-rolled steel:
The cold-rolled steel that step 4 is obtained carries out reverse transformation annealing at 650 DEG C, obtains having cold rolling compared with the annealing of high-ductility low
Medium carbon steel, obtains superplastic cold rolled annealed steel.
Step 6. superplasticity measures
Scheme a: carry out under experimental temperature shown in table 2 for the steel plate of the hot rolling 6mm thickness that step 2 is obtained and rate of extension
Superplastic tension is tested, and test steel is as shown in table 2 with the drawing by high temperature elongation percentage of compared steel.
Table 2 scheme a hot rolled steel plate drawing by high temperature superplastic ability
It can be seen from Table 2 that, invention steel has obtained the superplasticity of 170-392% after hot rolling, significantly larger than contrasts
The high-temp plastic of steel, illustrates that invention steel has superplasticity after hot rolling.This result also teaches that existing cp steel, dp steel simultaneously
There is no the superplasticity property of hot rolling supply of material state with industrialization middle low carbon steel iron products such as ph steel.
Scheme b: stretch under experimental temperature shown in table 3 for the cold-rolled steel sheet that step 4 is obtained and rate of extension, obtain height
Elongation percentage under temperature stretching is as shown in table 3.
The cold rolling amount of table 3 scheme b is 70% steel plate drawing by high temperature superplastic ability
It can be seen from Table 3 that, invention steel has obtained the superplasticity of 350-1510% after hot rolling, significantly larger than contrasts
The high-temp plastic of steel, illustrates that invention steel has superplasticity after cold rolling.This result also teaches that existing cp steel, dp steel simultaneously
There is no the superplasticity property of cold rolling supply of material state with industrialization middle low carbon steel iron products such as ph steel.
Scheme c: stretch under experimental temperature shown in table 4 for the cold-rolled steel sheet that step 5 is obtained and rate of extension, obtain height
Elongation percentage under temperature stretching is as shown in table 4.
The drawing by high temperature superplastic ability of table 4 scheme c reverse transformation annealing sheet material
It can be seen from Table 4 that, the cold rolling state steel plate of invention has obtained the super of 159-812% after reverse transformation annealing and has moulded
Property, the significantly larger than high-temp plastic of compared steel, illustrate that invention steel also has superplasticity after cold rolling and reverse transformation are annealed.Simultaneously
This result also teaches that the industrialization middle low carbon steel iron product such as existing cp steel, dp steel and ph steel does not have cold rolled annealed supply of material state
Superplasticity property.
Fig. 1 gave after 5# steel cold rolling 70% in 600-800 DEG C of superplastic temperature and deformation velocity 0.1-0.001/ second
Under the conditions of the superplastic tension assay maps that obtains.
Fig. 2 gives the superplastic tension curve of 6# steel cold rolling state sheet material.
Fig. 3 gives the change of specimen size before and after the superplastic tension of the cold rolling state of 6# steel.
Claims (3)
1. in low-carbon (LC) in a kind of high strain rate low-alloy superplasticity steel it is characterised in that chemical component weight percent is: c:
0.01-0.49%, mn:2.5-13.0%, al:0-12.0%, si:0-3.0%, cr:0-3.0%, ni:0-3.0%, balance of
Fe and inevitable impurity.
2. in low-carbon (LC) in high strain rate according to claim 1 low-alloy superplasticity steel it is characterised in that here is basic
Above separately descended a kind of or multiple element: mo:0-0.2%, nb:0-0.20%, ti:0-0.20%, v:0-0.20%, re:0-
0.20%.
3. in low-carbon (LC) in the high strain rate described in a kind of claim 1 or 2 low-alloy superplasticity steel preparation method, its feature
It is, technique includes smelting, casting, hot rolling, annealing and the process for making such as cold rolling, and the technical parameter controlling in process is such as
Under:
(1) smelting of steel and solidification: be applied to converter, electric furnace and induction furnace and smelt, produced using continuous casting strand or molding
Ingot casting；
(2) hot rolling of strand or ingot casting or hot continuous rolling or forging；
Hot continuous rolling sheet material: strand is heated through 1100-1250 DEG C, finish rolling after first roughing, carry out in the range of 300-700 DEG C after rolling
Coil into coil of strip, obtain the superplasticity hot-strip of industrialization supply of material state；
(3) soft annealing with cold rolling
Steel after thermal deformation are carried out in the range of 550-850 DEG C with soft annealing process to reduce steel plate hardness；After annealing
The different drafts carrying out 0-90% are cold rolling, obtain the cold rolling steel of superplasticity of industrialization supply of material state；
(4) the reverse transformation annealing of cold rolled sheet
Steel after cold roller and deformed are carried out making annealing treatment the room temperature high-ductility obtaining 20-50% in the range of 550-750 DEG C,
Obtain the cold rolled annealed steel of superplasticity of industrialization supply of material state.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107916359A (en) * | 2017-10-31 | 2018-04-17 | 华晨汽车集团控股有限公司 | A kind of preparation method of the medium managese steel with favorable forming property |
| CN110284042A (en) * | 2019-08-05 | 2019-09-27 | 西安工业大学 | Superplasticity high-entropy alloy, plate and preparation method thereof |
| CN113832320A (en) * | 2021-09-23 | 2021-12-24 | 钢铁研究总院 | Low-carbon low-alloy steel superplasticity material and preparation method thereof |
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| CN110284042B (en) * | 2019-08-05 | 2020-05-05 | 西安工业大学 | Superplastic high-entropy alloy, sheet and preparation method thereof |
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