CN106011653A - High-strength high-toughness low-density steel and manufacturing method thereof - Google Patents
High-strength high-toughness low-density steel and manufacturing method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 145
- 239000010959 steel Substances 0.000 title claims abstract description 145
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000000034 method Methods 0.000 claims abstract description 33
- 238000005098 hot rolling Methods 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims description 32
- 239000000203 mixture Substances 0.000 claims description 19
- 229910052782 aluminium Inorganic materials 0.000 claims description 15
- 241000186216 Corynebacterium Species 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 230000007704 transition Effects 0.000 claims description 3
- 238000011534 incubation Methods 0.000 claims 1
- 230000009286 beneficial effect Effects 0.000 abstract description 3
- 238000005516 engineering process Methods 0.000 abstract description 2
- 238000004321 preservation Methods 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract 1
- 229910052802 copper Inorganic materials 0.000 abstract 1
- 238000003754 machining Methods 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 229910052759 nickel Inorganic materials 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 24
- 229910001562 pearlite Inorganic materials 0.000 description 22
- 239000000463 material Substances 0.000 description 17
- 230000008569 process Effects 0.000 description 13
- 239000011572 manganese Substances 0.000 description 10
- 229910052742 iron Inorganic materials 0.000 description 9
- 208000037656 Respiratory Sounds Diseases 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 230000007246 mechanism Effects 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- 125000004429 atom Chemical group 0.000 description 4
- 238000003763 carbonization Methods 0.000 description 4
- 239000000470 constituent Substances 0.000 description 4
- 239000011229 interlayer Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910001234 light alloy Inorganic materials 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910018657 Mn—Al Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000012141 concentrate Substances 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000009413 insulation Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 210000003739 neck Anatomy 0.000 description 2
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- 238000005096 rolling process Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 206010011376 Crepitations Diseases 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 208000031481 Pathologic Constriction Diseases 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
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- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
Abstract
The invention provides high-strength high-toughness low-density steel and a manufacturing method of the steel. The method comprises the steps that the component of the steel to be rolled is controlled to comprise, by weight percent, 0.1% to 0.6% of C, 4.5% to 7.5% of Al, smaller than 10% of the sum of Mn, Cr, Mo, Ni and Cu and the balance Fe and inevitable impurity elements; the steel to be rolled is subject to hot rolling, cooling is carried out until phase change does not happen, and hot-rolled steel is obtained; the hot-rolled steel is heated to be lower than the critical temperature spot Acl by the section of 5 DEG C to 40 DEG C, and heat preservation is carried out by more than 6 h; and cooling is carried out, and the high-strength high-toughness low-density steel is obtained. The high-strength high-toughness low-density steel has the beneficial effects that the high-strength high-toughness low-density steel small weight and good in toughness matching can be obtained, the steel is suitable for the fields like the automobile industry, and the machining technology is simple and easy to control.
Description
Technical field
The invention belongs to steel material technical field, it relates in particular to one is applicable to such as automobile
Deng high intensity, high tenacity and the low-density steel in field, and manufacture this high-intensity high-tenacity low-density
The rolling of steel and heat treatment method.
Background technology
In recent years, for improving fuel efficiency and reducing greenhouse gas emission, want for reducing tare
Ask the most urgent.For meeting automaker to alleviating the demand of tare, traditional mesh of Materials
It is designated as high intensity high formability steel.But, this method being used for reducing tare depends on reduction material
Size, for keeping the rigidity of material, the method has certain limitation.The success of steel and iron industry is
While proof strength, do not lose other important engineering parameters such as toughness, rigidity.Density is for iron and steel
The improvement of performance makes iron and steel achieve the biggest success as structural material, each throughout daily life
Individual aspect.But, the density of ferrous materials is than emerging structural material, as aluminum, manganese alloy etc. are much larger,
Therefore, when paying close attention to structure lightened, if iron and steel only has high intensity, and its rigidity of structure does not obtain
When improving, it is unsatisfactory for the strategy of sustainable development.Low density steel is applied to body of a motor car, not only can be straight
Connect reduction tare, also can increase body stiffness.At present, high-intensity high-tenacity low density steel is at automobile
The application of industry has caused the biggest concern, many low density steels of planting to be developed.
The density of ferrous materials can by add light-alloy unit usually reduce, as aluminum (Al), silicon (Si),
(wherein, the density of Fe is 7.85gm cm to manganese (Mn) etc.-3, the density of Al is 2.7gm cm-3, Si
Density be 2.3gm cm-3, the density of Mn is 7.43gm cm-3).Its density reduces principle: add
On the one hand light-alloy element in steel expands the lattice parameter of steel and realizes volume increase, simultaneously light-alloy unit
Element atomic mass is relatively low, and two aspect combined factors effects realize density and reduce.Steel adds Al element improve
Ferrous materials competitiveness in auto industry is applied, beneficially automobile lightweight.
But, in the case of interpolation Al constituent content is higher in steel, hot-rolled steel toughness of material will be caused anxious
Fall sharply low (such as, breaking elongation is less than 13%, even below 8%), it is difficult to meets the necks such as such as automobile
The territory requirement to steel toughness.
Summary of the invention
It is an object of the invention to solve at least one in deficiencies of the prior art.
Such as, an object of the present invention be to provide one be suitable for the field such as such as automobile steel use,
There is high aluminium content and the manufacture method of the good high-intensity high-tenacity low density steel of toughness.
Inventor it has been investigated that, in Fe-C-Mn-Al system steel alloy add the higher (example of Al constituent content
As, 5%, 6%, 8% etc.) in the case of, often can be along with the Kappa carbide (letter of perovskite structure
It is referred to as κ carbide) occur, its chemical formula is Al (Fe, Mn)3C, wherein Al atom is positioned at cubic cell
On angle, Fe atom and Mn atom are positioned at structure cell center of area position, C atom be positioned at structure cell center (by Fe and
The octahedron of Mn atomic building).κ carbide and about relative to steel (or claim alloy) deformation process
In the impact of fracture mechanism the biggest.When austenite and κ carbide coexist, the most initial and extension is split
Stricture of vagina, thick κ carbide generation cleavage fracture, austenite and κ carbide interface (are also denoted as Austria
Family name's body/κ carbide interface) peeling-off, micro-crack, then across thick κ Carbide Phases, expands along interface
Exhibition.And κ carbide and ferrite are when coexisting, most of crackles are formed at κ carbide strip interface, κ
Carbide is strip shape continued presence, and strip shape κ carbide primarily forms position as crackle.Thus,
Cause the hot-finished material toughness containing higher Al content poor.
Based on foregoing, an aspect of of the present present invention provides the system of a kind of high-intensity high-tenacity low density steel
Make method, said method comprising the steps of: the composition controlling steel to be rolled is by weight percentage: C:
0.1～0.6%, Al:4.5～7.5%, Mn+Cr+Mo+Ni+Cu sum less than 10% and surplus
Fe and inevitable impurity element；Treat rolled steel and carry out hot rolling, be cooled to no longer undergo phase transition,
Obtain hot-rolled steel；Hot-rolled steel is heated to less than critically weighted Ac15～40 DEG C of intervals below, are incubated 6h
Above；Cooling, obtains high-intensity high-tenacity low density steel.
Another aspect provides a kind of high-intensity high-tenacity low density steel, described high intensity and high ductility
The composition of property low density steel is by weight percentage: C:0.1～0.6%, Al:4.5～7.5%, Mn+Cr
+ Mo+Ni+Cu sum less than 10% and the Fe of surplus and inevitably impurity element, and
The microscopic structure of described high-intensity high-tenacity low density steel is by ferrite and the corynebacterium interspersed among on ferrite
And/or near-spherical κ carbide composition.
Compared with prior art, the beneficial effect comprise that the lightweight effect utilizing Al element,
By steel add Al element, it is thus achieved that low-density steel, have a good application prospect and (such as apply
In auto industry, can directly reduce tare, improve ferrous materials competition in auto industry is applied
Power)；By the control proportioning of reasonable C content and Al content, it is ensured that in the low-density of steel and tissue
Carbide morphology and ratio, and Al constituent content add heterogeneous microstructure develop driving force, shorten
Evolution time；The elongation percentage of steel rises to > 18%, it will be apparent that improve material plasticity, steel product microcosmic
Uniform texture and be ferrite+corynebacterium/near-spherical κ carbide；Processing technique simplicity is easy to control,
Requirement without cooling rate, it is easy to accomplish.
Accompanying drawing explanation
Fig. 1 shows the microscopic structure of the hot-rolled steel of the exemplary enforcement of the present invention.
Fig. 2 shows pattern near the stretching fracture of the hot-rolled steel of the exemplary enforcement of the present invention.
What Fig. 3 showed the hot-rolled steel of the exemplary enforcement of the present invention adds thermal dilatometry, wherein, and Ac1For phase
Become and start temperature, Ac3For phase transformation end temp.
Fig. 4 shows heating and the heat preservation method schematic diagram of exemplary embodiment of the present, wherein, HR table
Show hot rolling.
Fig. 5 shows the microstructure of the high-strength and high ductility low density steel of the exemplary enforcement of the present invention.
Fig. 6 shows that the hot-rolled steel of the exemplary enforcement of the present invention and high-strength and high ductility low density steel are at normal temperatures
Engineering stress-strain curve.
Fig. 7 shows shape near the stretching fracture of the high-strength and high ductility low density steel of the exemplary enforcement of the present invention
Looks.
Detailed description of the invention
Hereinafter, low close to the high-intensity high-tenacity describing the present invention in detail by combining exemplary embodiment
Degree steel and manufacture method thereof.
Generally speaking, the present invention is that inventor requires to obtain fields such as being suitable for such as automobile steel
High-intensity high-tenacity low density steel, composition based on high-carbon high alumina design and the microcosmic to this composition hot-rolled steel
Organizational structure and the specificity analysis of fracture mechanism and subsequent heat treatment operation are to this composition hot-rolled steel microcosmic
The research such as the impact of organizational structure and fracture mechanism and discovery, and consider composition, processing technique, heat
Process technique etc., the creative work of experience hardships and draw.
In the present invention, steel to be rolled need to be controlled and there is the composition of high-carbon high alumina.Wherein, C content exists
Between 0.1～0.6%, Al content is between 4.5～7.5%.Preferably, C with Al content sum is not less than
5%.C is the element that primarily forms of carbide, higher C content, coordinates the aluminum content of the present invention to protect
κ carbide/the pearlite of card larger proportion exists.Alloy increases C content, it is possible to decrease hot rolling microstructure is thick
The probability that big interfacial carbide thing occurs, and interfacial carbide thing would generally in deformation initial crack, cause
Cracking, causes poor toughness.After C content increases, the thick carbide that interface goes out is by graininess or thin film
Shape carbide replaces, and the probability that crackle starts reduces, and can obviously improve hot-strip toughness.Al is ferrum
Ferritic stable element, it is ensured that a large amount of existence that in tissue, ferritic phase is stable.Additionally, Al is the present invention
Fe-C-Mn-Al system alloy in κ carbide primarily form element, determine the formation amount of κ carbide.
Compared with Al with Fe atom, for light element, steel adds aluminum due to metathesis can reduce atomic mass and
Expand lattice parameter, thus reduce the density of steel, it is achieved lightweight.Steel adds Al content 4.5～7.5%
Between, it is possible to decrease the density of steel, its addition more about advantageously reduces the density of steel.
In the present invention, the hot rolling low-density steel that steel to be rolled obtains after hot rolling (may be simply referred to as heat
Steel rolling) initial microstructure include: ferrite, Kappa pearlite (referred to as κ pearlite), with
And κ carbide, wherein, κ carbide can be located at ferrite interface, and/or is positioned at ferrite and κ pearly-lustre
Body interface.κ pearlite is formed by between the κ carbide of sheet and ferritic phase.κ pearlite and θ pearly-lustre
Body is compared has higher intensity, bigger fragility.According to Hall-Petch relation, the intensity of pearlite
Reduce with sheet interlayer spacing with hardness and increase.Al diffusion necessary in κ pearlite forming process reduces plate
Bar thickens kinetics, thus has refined κ pearlite interlaminar spacing, adds κ pearlite intensity.Due to
The characteristic of κ carbide itself, even if in the case of sheet interlayer spacing is identical, the intensity of κ pearlite also above
θ pearlite.And the Al content of the present invention is limited between 4.5～7.5%, higher Al content increases altogether
Phase separation height carbon content, improves the carbide proportion in pearlite.The sheet interlayer spacing that κ pearlite is thinner
Bigger carbide proportion so that it is there is higher intensity and fragility.
Hot rolling low-density steel in the present invention have poor toughness.Fracture the initial stage, ferrite with
κ carbide interface (being also denoted as ferrite/κ carbide interface) place or the κ carbon of ferrite grain boundaries
Easy initial crack at compound, this is due under identical stress condition, the ferrite of soft phase and hard phase κ carbonization
The dependent variable of thing is different, forms certain internal stress so that in two phase boundaries between ferrite and κ carbide
Crackle it is easily formed at face.Along with stress increases, cracks produces strong stress and concentrates, and crackle is along ferrum element
, there is interface peel in body/κ carbide interface extension, stress continues to increase, and big cracks can spread enters ferrite
Or inside κ pearlite.Due to the fragility that κ pearlite is bigger, material rapid crack propagation, cause in the present invention
Hot rolling low-density steel toughness poor.
Composition range based on high-carbon high alumina and to the heterogeneous microstructure of this composition hot-rolled steel and fracture machine
The characteristic of reason, this composition hot-rolled steel, through researching and proposing, is heated to a certain temperature range (i.e., by inventor
Less than Ac1The temperature range of 5～40 DEG C below temperature) and it is incubated more than 6h in this temperature range, it is preferable that
It is incubated 8～144 hours (such as, optional 6,12,36,72 hours etc. time), subsequently by arbitrarily side
Formula cools down, thus obtains the high-intensity high-tenacity low density steel product that toughness significantly improves.Aforementioned
Heating and isothermal holding, it is possible to the κ Carbides Evolution making sheet is near-spherical and/or corynebacterium, from
And it is obtained in that microscopic structure is by ferrite and the corynebacterium interspersing among on ferrite and/or the carbonization of near-spherical κ
The high-intensity high-tenacity low density steel product that thing is constituted, improves steel toughness, and improve its formability from
And be easy to be processed further, this is conducive to the requirement to steel such as such as automobile steel.And, the present invention
Composition of steel in Al content, beneficially eutectoid point carbon content increases, thus is conducive to obtaining further strong
The steel that toughness coupling is good.
In the present invention, the mechanism that κ Carbides Evolution is near-spherical and/or corynebacterium of sheet is generally:
Thermodynamic driving force comes from the reduction of interfacial free energy between κ carbide and iron matrix ferritic, and kinetics is driven
Power is to be caused its unit at interface between κ carbide and iron matrix ferritic by the uneven distribution of alloying element
Element diffusion provides.Due to the existence of concentration of element difference, the alloying element in κ carbide needs little from radius
Region (at banding top and thin neck) diffuse to the region that radius is bigger, in this way, carbonization
Thing ruptures, and is accumulated into particle.The nodularization process of carbide mainly includes two stages, i.e. κ carbide plate
Bar fracture and carbide particle are roughened.In the present invention, the interpolation of 4.5～7.5%Al elements has refined κ pearlite
Sheet interlayer spacing, add the driving force that κ pearlite is developed to near-spherical and/or corynebacterium by sheet,
Additionally, Al content also improves Ac1Temperature, thus shorten κ pearlite by sheet to near-spherical and/or
Corynebacterium evolution time.The κ carbide of sheet is after aforementioned heating and isothermal holding, and length reduces,
Size reduces, and the stress of interface is concentrated and reduced, simultaneously because its less size, stress is difficult to load
On carbide, it is achieved toughness improves.High-intensity high-tenacity low density steel product of the present invention has good
Intensity (such as, being not less than 560MPa) and plasticity (such as, elongation percentage improve to > 18%).
In one exemplary embodiment of the present invention, the manufacture method of high-intensity high-tenacity low density steel can
Realized by following steps.
First, the composition controlling steel to be rolled is by weight percentage: C:0.1～0.6%, Al:
4.5～7.5%, Mn+Cr+Mo+Ni+Cu sum is less than 10% and the Fe of surplus and can not keep away
The impurity element exempted from.Further, it is possible to control the C element content in steel to be rolled be 0.35～0.50%,
Al:5.0～6.8%.Steel to be rolled can be continuous casting billet or casting base.
Then, treating rolled steel and carry out hot rolling, heat temperature processed can be in the range of 1100 DEG C～900, but not
It is limited to this, it is also possible to properly increase (such as, 1150 DEG C) or reduce (such as, 870 DEG C) hot-rolled temperature,
Being appropriate can normally complete hot-rolled process, subsequently, cooling (such as, air cooling) is to no longer undergoing phase transition
(such as, it is cooled to compare Ac1Arbitrary temperature of low less than 200 DEG C of temperature), obtain hot-rolled steel.Concrete next
Saying, the microscopic structure of the hot-rolled steel that hot-rolled step obtains by volume mark meter can be by the κ carbonization not less than 4%
The ferrite of the body-centered cubic structure of thing, cementite less than 2% and surplus is constituted.Here, hot rolling
Steel includes but not limited to the kinds such as hot rolled plate, hot rolled coil, Bar Wire Product, shaped steel and Wide and Thick Slab.
It follows that hot-rolled steel is heated to less than critically weighted Ac15～40 DEG C of intervals below, are incubated 6h
Above.Preferably, hot-rolled steel is heated to less than its critically weighted Ac110～30 DEG C of intervals below, protect
Temperature 10～144h.
Cool down subsequently, obtain high-intensity high-tenacity low density steel.Here it is possible to use any type of cooling
It is cooled to obtain high-intensity high-tenacity low density steel product.
In another exemplary embodiment of the present invention, the composition of high-intensity high-tenacity low density steel is by weight
Amount percentage ratio can be: C:0.1～0.6%, Al:4.5～7.5%, Mn+Cr+Mo+Ni+Cu it
With less than 10% and the Fe of surplus and inevitable impurity element, and high-intensity high-tenacity is low close
The microscopic structure of degree steel is by ferrite and the corynebacterium interspersed among on ferrite and/or near-spherical κ carbide group
Become.Preferably, the length of corynebacterium κ carbide is not more than 10 μm；Described near-spherical κ carbide is
Big radial dimension is not more than 4 μm.The density of the high-intensity high-tenacity low density steel of the present invention is less than
7.5g cm-3(even less than 7.3g cm-3) and elongation percentage be not less than 18%.
The concrete example of the present invention is described more fully below to further illustrate the exemplary enforcement of the present invention
Example.
Table 1 shows that the chemical composition of steel to be rolled (No. 1 strand and No. 2 strands) is constituted and density
With κ carbide volume fraction situation.
The chemical composition of table 1 steel to be rolled and density thereof and κ carbide volume fraction
The steel to be rolled (No. 1 strand and No. 2 strands) of chemical composition shown in table 1 is heated to
1150～1250 DEG C, insulation 0.5～2h carries out homogenizing process, then through 1100 DEG C～900 DEG C of hot rollings, hot rolling
Rear acquisition thickness of slab is the hot-rolled steel of 4mm.
As shown in table 1, the density of No. 1 strand and the hot-rolled steel corresponding to No. 2 strands is respectively
7.30g·cm-3With 7.12g cm-3, it is below 7.5g cm-3；The volume fraction of κ carbide is respectively 7.8
Vol.% and 4.2 vol.%, is all higher than 4%.Hot-rolled steel microscopic structure such as Fig. 1 institute corresponding to No. 1 strand
Showing, understanding the high alumina hot rolling low density steel microstructure observation in Fig. 1, its microscopic structure is by banding ferrum
Ferritic, banding pearlite, and ferrite interface, and/or it is positioned at ferrite and pearlite interface
κ carbide forms.
After hot-rolled steel stretch broken test corresponding to No. 1 strand, the such as Fig. 2 of the pattern near its fracture
Shown in.As shown in Figure 2, its crackle results from κ carbide and ferrite interface more.Obviously, disconnected
Split the initial stage, formed at ferrite with κ carbide interface or at the strip κ carbide of ferrite grain boundaries
Micro-crack, along with stress increases, cracks produces strong stress and concentrates, and crackle is along ferrite/κ pearly-lustre
Body interface extends, and interface peel occurs, and stress continues to increase, and big cracks can spread enters ferrite or κ pearly-lustre
Internal portion.Due to the fragility that κ pearlite is higher, rapid crack propagation after cracks can spread.Wherein, κ pearlite
The lamellar tissue being arranged alternately with each other for sheet κ carbide and ferrite.
Hot-rolled steel corresponding to No. 1 and No. 2 strands is carried out respectively swellability measurement, and surveys based on dilatometer
Fixed respective starting temperature of transformation (Ac1), so that it is determined that hot-rolled steel is heated and during isothermal holding
Holding temperature.No. 1 and hot-rolled steel respective starting temperature of transformation A corresponding to No. 2 strandsc1Respectively may be about
714 DEG C and 698 DEG C.The expansion curve of the hot-rolled steel corresponding to No. 1 strand as it is shown on figure 3, wherein, Ac1
For starting temperature of transformation, about 714 DEG C, Ac3For phase transformation end temp, about 1076 DEG C.To hot-rolled steel
The process of heating and isothermal holding that carries out is as shown in the step curve on right side in Fig. 4.
Table 2 shows holding temperature and the temperature retention time of hot-rolled steel.As shown in table 2, with No. 1 strand institute
Corresponding hot-rolled steel forms 3 samples (being designated as sample 1A, 1B and 1C respectively)；With No. 2 strand institutes
Corresponding hot-rolled steel forms 3 samples (being designated as sample 2A, 2B and 2C respectively).To sample 1B, 1C,
2B and 2C carries out isothermal holding, and its holding temperature and temperature retention time are as shown in table 2.It addition, such as table 2
Shown in, sample 1A and 2A does not carry out heating and isothermal holding.
The holding temperature of table 2 hot-rolled steel and temperature retention time
Sample 1B is heated to 700 DEG C and is incubated 16h, and cooling subsequently obtains target steel.This target steel
As it is shown in figure 5, as shown in Figure 5, the microscopic structure of target steel is ferrite+stub to the microscopic structure of material
Shape and/or near-spherical κ carbide, and the length of corynebacterium κ carbide is all not more than 10 μm, class ball
The maximum radial dimension of shape κ carbide is all not more than 4 μm.
After process warm to sample 1B, 1C, 2B and 2C the target steel of gained and sample 1A and
2A carries out Mechanics Performance Testing respectively, and its respective mechanical property is as shown in table 3.Sample 1B is through protecting
Temperature process after the target steel mechanics performance (as shown in the dotted line in Fig. 6) of gained and the power of sample 1A
Learning performance (shown in solid as in Fig. 6) Comparative result as shown in Figure 6, tensile sample is gauge length 50mm
ASTM standard sample.Obviously, hot-rolled steel (such as, the sample 1A of present component is only met
And 2A) elongation percentage relatively low (such as, 13% and 8%)；And through based on present component and in hot rolling
After through heating and thermal insulation process (such as, the warm process of sample 1B, 1C, 2B and 2C of target steel
The target steel of rear gained) then there is good toughness (such as, 24%, 28%, 19% and 32%),
And there is more preferable tough matching.
The tensile mechanical properties of table 3 steel plate
After process warm to sample 1B, the target steel of gained carry out tension failure test, its tension failure
Pattern near rear fracture is as shown in Figure 7.As seen from Figure 7, its crackle is both formed in ferrite base
At body and κ carbide interface.Intensity, less size and the near-spherical higher due to κ carbide and/or
Rod-like shape, stress is difficult to be loaded into κ carbide, is difficult to continue extension during cracks can spread to κ carbide.
Microstructure evolution after heated and isothermal holding changes the fracture mechanism in deformation process, so that toughness
Be improved significantly.
In sum, the beneficial effect comprise that
1, the present invention utilizes the lightweight effect of Al element, by adding Al element in steel, it is thus achieved that low
Dense steel, has a good application prospect；
2, by the control proportioning of reasonable C content and Al content, it is ensured that in the low-density of steel and tissue
Carbide morphology and ratio；And Al constituent content adds the driving force that heterogeneous microstructure develops, contracting
Short evolution time；
3, the elongation percentage containing κ carbide low density steel of the present invention rises to > 18%, it will be apparent that improve material
Material plasticity, the steel product heterogeneous microstructure of the present invention uniformly and is ferrite+corynebacterium/near-spherical κ
Carbide；
4, the processing technique simplicity of the present invention is easy to control, without cooling rate requirement, it is easy to accomplish.
Although describing the present invention already in connection with accompanying drawing and exemplary embodiment above, but this area being common
Technical staff, can be to above-mentioned it should be clear that in the case of without departing from spirit and scope by the claims
Embodiment carries out various amendment.
Claims (7)
1. the manufacture method of a high-intensity high-tenacity low density steel, it is characterised in that described method includes
Following steps:
The composition controlling steel to be rolled is by weight percentage: C:0.1～0.6%, Al:4.5～7.5%,
Mn+Cr+Mo+Ni+Cu sum is less than 10% and the Fe of surplus and inevitable impurity is first
Element；
Treat rolled steel and carry out hot rolling, be cooled to no longer undergo phase transition, obtain hot-rolled steel；
Hot-rolled steel is heated to less than critically weighted Ac15～40 DEG C of intervals below, are incubated more than 6h；
Cooling, obtains high-intensity high-tenacity low density steel.
2. according to the manufacture method of the high-intensity high-tenacity low density steel described in claim, it is characterised in that
The microscopic structure of described hot-rolled steel by volume mark meter is by the κ carbide not less than 4%, oozing less than 2%
The ferrite of the body-centered cubic structure of carbon body and surplus is constituted.
The manufacture method of high-intensity high-tenacity low density steel the most according to claim 1, its feature exists
In, the time of described incubation step is 6～144h.
4. according to the manufacture method of the high-intensity high-tenacity low density steel described in claim, it is characterised in that
Described hot-rolled steel includes hot rolled plate, hot rolled coil, Bar Wire Product, shaped steel and Wide and Thick Slab.
5. a high-intensity high-tenacity low density steel, it is characterised in that described high-intensity high-tenacity low-density
The composition of steel is by weight percentage: C:0.1～0.6%, Al:4.5～7.5%, Mn+Cr+Mo+Ni
+ Cu sum less than 10% and the Fe of surplus and inevitably impurity element, and described high-strength
The microscopic structure of degree high tenacity low density steel is by ferrite and the corynebacterium interspersed among on ferrite and/or class
Spherical κ carbide forms.
6. want the high-intensity high-tenacity low density steel described in 5 according to right, it is characterised in that described stub
The length of shape κ carbide is not more than 10 μm；The maximum radial dimension of described near-spherical κ carbide is not more than
4μm。
High-intensity high-tenacity low density steel the most according to claim 5, it is characterised in that described height
The density of strength high toughness low density steel is less than 7.5g cm-3And elongation percentage is not less than 18%.
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