CN110062814A - Low alloy steel plate with excellent intensity and ductility - Google Patents

Low alloy steel plate with excellent intensity and ductility Download PDF

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Publication number
CN110062814A
CN110062814A CN201780076526.XA CN201780076526A CN110062814A CN 110062814 A CN110062814 A CN 110062814A CN 201780076526 A CN201780076526 A CN 201780076526A CN 110062814 A CN110062814 A CN 110062814A
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alloy steel
steel plate
steel
phase
low alloy
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崔点镕
朴美男
李敏亨
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Posco Holdings Inc
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Posco Co Ltd
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite
    • 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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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

Disclose a kind of low-alloy steel, the low-alloy steel reduces face checking during hot rolling by minimizing the addition of alloying element, and at the same time ensuring corrosion resistance by the way that Cr is used as one of main component and designing by high Mn to realize TRIP or TWIP phenomenon, to have excellent hot-workability, high intensity and high ductibility.An embodiment according to the present invention, low alloy steel plate with excellent intensity and ductility includes in terms of the weight percent (%) of total composition: 0.05% to 0.3% C, 0.7% to 2.5% Si, 8% to 12% manganese Mn, 13% to 15.5% Cr, 0.5% to 3.0% Cu, 0.1% to 0.2% N, 0.25% or less aluminium Al, 0.25% or less tin (Sn), and rest part is iron (Fe) and other inevitable impurity.The microscopic structure of low alloy steel plate includes using in volume fraction 5% or less ferritic phase and/or martensitic phase as microscopic structure, and rest part includes austenite phase.

Description

Low alloy steel plate with excellent intensity and ductility
Technical field
This disclosure relates to it is suitable for the high intensity of the structural material of such as automobile and railroad track and the steel plate of high ductibility, And more particularly it relates to by keeping alloying element such as Ni minimized and being controlled using Cr and Mn as main component Microscopic structure processed and make intensity and the excellent low alloy steel plate and its manufacturing method of ductility.
Background technique
The weight for mitigating body of a motor car using high-intensitive and high ductibility steel plate is continued.In recent years, it has opened Send out and used phase-change organization's steel of the excellent workability compared with existing precipitation strength steel or Solid Solution Strengthened Steel.Phase-change organization Steel is using DP (two-phase) steel, TRIP (phase-change induced plastic) steel and CP (compound phase) steel as representative.The mechanical performance of phase-change organization's steel, As tensile strength and elongation percentage level change according to the type and score of the shape of parent phase and the second phase respectively.
During TRIP steel as one of phase-change organization's steel forms the cooling treatment after austenite during annealing It can control both cooling rate and cooling termination temperature, to partly mention and making austenite fraction remaining at room temperature High-intensitive and ductility.Metastable state retained austenite passes through deformation at martensite, thus by being prolonged with increased intensity The relaxations of slow stress raisers and constriction increase elongation percentage.It is important, therefore, that TRIP steel is remaining more than one at room temperature Determine the austenite of score.For this purpose, among the austenite stabilizing elements should be added together with a large amount of Mn, to keep certain at room temperature The retained austenite of percentage.
On the other hand, there are TWIP (twinning induced plasticity) steel, TWIP steel by added in steel a large amount of C and Mn and Above-mentioned phase transformation textured steel and constitute austenite one phase.In the case where TWIP steel, TWIP steel show excellent tensile strength and Elongation percentage.But when the content of C in TWIP steel be by weight 0.4% when, unless the content of Mn be by weight about 25% or It is bigger, it otherwise cannot steadily obtain the austenite for causing twinning.Moreover, when the content of C in TWIP steel is by weight When 0.6%, unless the content of Mn is by weight about 20% or bigger, austenite otherwise cannot be steadily obtained.In addition, Ying Tian Add a large amount of among the austenite stabilizing elements, so that austenite steadily exists at room temperature, because foring to machinability extremely The ε martensite (ε) of unfavorable HCP structure and the martensite (α ') of BCT structure.
PCT Publication patent application the 2012/077150th be related to it is a kind of with excellent mechanical performance and formability The TWIP steel of high Mn content, and the patent application includes the cold rolled annealed steel for cold annealing and recrystallization heat treatment.At this In patent document, it is additionally supplemented with alloying element such as C, Al and Si, so that austenite phase is stable or controls stacking defect energy (SFE)。
As described above, add the TWIP steel of a large amount of alloy compositions and TRIP steel is solidified into austenite one phase during fabrication, heat Processability is weakened, and the defect as caused by aluminium as field trash is easy to happen in hot rolling.It has the disadvantage that, manufactures skill Art (such as casting and rolling process) is because very difficult there are problem, and manufacturing cost being significantly increased because of cost of alloy And it is higher.
The patent disclosure the 2012-077150th (on June 14th, 2016) of (patent document 0001) PCT Publication
Summary of the invention
Technical problem
The present invention minimizes the addition of alloying element to reduce face checking during hot rolling, by based on constructing Cr One of component is wanted to ensure corrosion resistance and realize TRIP or TWIP phenomenon by high Mn design, to provide with excellent The low alloy steel plate of different hot-workability, intensity and ductility.
Technical solution
According to an aspect of the present invention, a kind of intensity and the excellent low alloy steel plate of ductility include with the weight of total composition Percentage (%) meter: 0.05% to 0.3% carbon (C), 0.7% to 2.5% silicon (Si), 8% to 12% manganese (Mn), 13% to 15.5% chromium (Cr), 0.5% to 3.0% copper (Cu), 0.1% to 0.2% nitrogen (N), 0.25% or less Aluminium (Al), 0.25% or less tin (Sn), and rest part is iron (Fe) and other inevitable impurity, wherein it is low The microscopic structure of alloy-steel plate include volume fraction be 5% or at least one of less ferritic phase and martensitic phase, and And rest part includes austenite phase.
Low alloy steel plate can also include 0.2% or less nickel (Ni).
Low alloy steel plate can also include 0.2% or less molybdenum (Mo).
The elongation percentage of low alloy steel plate can be 40% or bigger.
The tensile strength of low alloy steel plate can be for 650MPa or bigger.
Beneficial effect
The excellent low alloy steel plate of the intensity and ductility of each embodiment according to the present invention by realize TRIP or TWIP phenomenon and there is 650MPa or bigger tensile strength and 40% or bigger elongation percentage, and can be used for automobile component Or other structural materials.
In addition, low alloy steel plate includes the Cr and tool as one of main component according to each embodiment of the disclosure Excellent corrosion resistance makes the addition of alloying element minimize and be excellent in terms of hot-workability.
Detailed description of the invention
Fig. 1 to Fig. 4 is to show carrying out to steel of the invention with steel is compared for an embodiment according to the present invention The photo of the degree of crack at edge occurs in hot rolling.
Fig. 5 to Figure 10 is steel of the invention after the thermal annealing of an embodiment according to the present invention and compares steel The light micrograph of microscopic structure.
Figure 11 to Figure 14 is to show the microscopic structure steel 9 according to the present invention of an embodiment according to the present invention The light micrograph that hot-roll annealing temperature changes.
Figure 15 is the steel of the invention for showing an embodiment according to the present invention and the tension test knot for comparing steel The figure of fruit.
Preferred forms
According to the intensity of the disclosure embodiment and ductility, excellent low alloy steel plate be may include with total group At weight percent (%) meter: 0.05% to 0.3% carbon (C), 0.7% to 2.5% silicon (Si), 8% to 12% Manganese (Mn), 13% to 15.5% chromium (Cr), 0.5% to 3.0% copper (Cu), 0.1% to 0.2% nitrogen (N), 0.25% or Less aluminium (Al), 0.25% or less tin (Sn), and rest part is iron (Fe) and other inevitable impurity.It is low The microscopic structure of alloy-steel plate may include volume fraction as at least one in 5% or less ferritic phase and martensitic phase Person, and rest part includes austenite phase.
The embodiment of invention
Hereinafter, it will be described in detail with reference to the accompanying drawings the embodiment of the disclosure.Following implementation is provided with by this public affairs The technical concept opened is communicated to those of ordinary skill in the art.However, the present disclosure is not limited to these embodiments, and the disclosure It can implement in another form.In the accompanying drawings, the part unrelated with describing may be not shown to illustrate the disclosure, and in addition, For ease of understanding, the size of component is more or less large shown.
The excellent low alloy steel plate of the intensity and ductility of an embodiment according to the present invention includes with total composition Weight percent (%) meter: 0.05% to 0.3% carbon (C), 0.7% to 2.5% silicon (Si), 8% to 12% manganese (Mn), 13% to 15.5% chromium (Cr), 0.5% to 3.0% copper (Cu), 0.1% to 0.2% nitrogen (N), 0.25% or more Few aluminium (Al), 0.25% or less tin (Sn), and rest part is iron (Fe) and other inevitable impurity.
Below by the effect to each component for including in the excellent low alloy steel plate of intensity according to the present invention and ductility It is described with content.Hereinafter, % refers to weight %.
C:0.05 to 0.3%.
Carbon is austenite former and is effective element for increasing the intensity of material by solution strengthening.To the greatest extent Pipe adds a large amount of C to ensure that high intensity is advantageous, but when excessively adding C, corrosion resistance is reduced, therefore the upper limit It is constrained to 0.3%.On the other hand, lower limit is constrained to 0.05%, to consider the decarburization load during melting and obtain with most A small amount of C increases the effect of intensity.Preferably C of addition in the range of 0.05% to 0.3%, by adding C come really It protects intensity and ensures stable production.
Si:0.7% to 2.5%
Silicon is partly added, because silicon has deoxidation effect and is ferritic stabilizer.But if silicon is excessive, Then mechanical performance relevant to corrosion resistance and impact flexibility will deteriorate.When adding a large amount of Si, ferrite content increase with Cause face checking during hot rolling, and there are problems that during manufacture rolling load increase, therefore, ceiling restriction at 2.5%.On the other hand, lower limit is constrained to 0.7%, controls stability, the controlled strain of austenite phase will pass through addition Si The formation of induced martensite and easy to produce.In order to control phase fraction and control austenite phase transformation phase by addition Si Between deformation mechanism, preferably by the scope limitation of Si 0.7% to 2.5%.
Mn:8% to 12%
Manganese is austenite former and is the essential element for constituting the austenite phase in the steel for adding Cr.Particularly, Cu is used as the substitute element of Ni.In the case where containing a large amount of Mn in production, the field trash based on oxide causes production to lack It falls into or corrosion resistance deteriorates.It reduces field trash and needs other technology, such as to reduce the special refining of dissolved oxygen, and manufacture Increased costs.Therefore, ceiling restriction is at 12%.For adding the minimum of Ni and for ensuring austenite one phase or some iron The minimum of ferritic or martensitic structure is about 8%.Therefore, the range of Mn is preferably constrained to 8% to 12%.
Cr:13.0% to 15.5%
Chromium is representative ferrite former and is the element for increasing corrosion resistance.Particularly, chromium is greatly Influence the element of nitrogen solubility.In order to minimize the face checking during hot rolling, preferably when being solidified with ferrite Initial phase is controlled, in order to avoid controlling microelement using extremely low level, particularly as the S and P of intercrystalline segregation element.When iron element When the amount of body is more than a certain amount of, ferrite is present at high temperature in ferrite and austenite two-phase, so as to cause hot-workability Deterioration and a large amount of crackle is generated in hot rolling.In addition, existing in the manufacture of final products than required ferritic phase More some ferritic phases, lead to the deterioration of mechanical performance.Therefore, the ceiling restriction of Cr is at 15.5%.On the other hand, when Cr's When content is too low, solidified when existing by solidifying at high temperature using austenite initial phase to control as intercrystalline segregation source The problem of amount of P and S.If above-mentioned control is insufficient, a large amount of face checking will occur in the fabrication process.In addition, wanting At least 13.0% chromium is sought, to obtain the smallest corrosion resistance and to the excellent anticorrosive of carbon steel.It is therefore preferred that by Cr's Content is constrained to 13.0% to 15.5%, the ferrite to be solidified into initial phase in the range of required alloying element and Keep the corrosion resistance of minimum stainless steel grade.
Cu:0.5% to 3.0%
Copper is analogous to the austenite former of Mn and Ni.As the element for replacing Ni and adding, when Cu is excessively added Added-time can be precipitated for Cu, to lead to embrittlement of grain boundaries when heated because being more than solubility.Therefore, dissolution can be no more than The maximum level that the stability of austenite is controlled in the case where degree is 3.0%.On the other hand, minimum content 0.5%.Work as content When less than 0.5%, addition Cu is nonsensical and will not influence the stability and formation of austenite.Therefore, Cu is preferably limited It is made 0.5% to 3.0%.
N:0.1% to 0.2%
Nitrogen is representative austenite former together with Ni, and nitrogen is the corrosion resistant for improving material together with Cr and Mo The element of corrosion.(content shows the additive effect of N and improves the material with interstitial element together with C minimum N content Intensity) it is 0.1%.In general, applying pressure to increase the solubility of N, to dissolve a large amount of N in material.Even if as Cr and Mn for increasing the representative element of the solubility of N largely exist, but can in the case where not applying atmospheric pressure The amount of the N farthest dissolved is 0.2%.It is preferred, therefore, that suitable N is limited in the range of 0.1% to 0.2%.
Al:0.25% or less
Aluminium is the ferrite former in the stainless steel for add Cr and is for carrying out the useful of deoxidation in steel-making Element.Also, it is known that the stacking defect that Al increases austenite phase when modified can be to form strain inducing martensite or machine Tool twin, and improve delayed fracture resistance, that is, the crackle generated after molding.If Al content is more than 0.25%, generate Biggish Al base field trash simultaneously leads to surface defect.In addition, can then contain a large amount of iron at high temperature when excessively adding Al Ferritic phase, this causes to crack during hot rolling.Therefore, the content of Al is constrained to 0.25%.
Sn:0.25% or less
Tin is known as being to improve material by controlling the thickness of anneal oxidation skin (annealing scale) during annealing The corrosion resistance of material and the element for improving pickling performance.In other words, when adding Sn, inhibition can be improved in cold rolling or hot rolling SiO is formed on the scale surface layer generated in annealing2The effect of oxide, and cold rolled annealed processing can be improved Efficiency.However, the reduction that the deterioration and production process that will lead to hot-workability is excessively added of Sn, thus ceiling restriction at 0.05%.In addition, when adding Sn, Sn is added to the surface of the passivation layer of stainless steel to increase and apply for corrosion resistance The patience of layer.Therefore, the content of Sn is limited in the range of 0.05%.
An embodiment according to the present invention, low alloy steel plate can also contain 0.2% in terms of weight percent % Or less Ni and/or 0.2% or less Mo.
Nickel is austenite former and plays the role of identical with Mn.Most of Ni are replaced by Mn, and some nickel Exist as impurity such as waste material (scrap).The residual quantity of Ni is constrained to 0.2%.
Molybdenum is to increase corrosion resistance and the ferritic expensive element of formation.The content of Mo is constrained to 0.2%.
The low alloy steel plate according to the present invention for meeting alloying element compositing range has volume fraction in microscopic structure For 5% or at least one of less ferritic phase and martensitic phase, and rest part includes austenite phase.In addition, root The inevitable precipitated phase in addition to ferritic phase and martensitic phase, but its body can be contained according to low alloy steel plate of the invention The sum of fraction is 5% or smaller.
Low alloy steel plate according to the present invention can be according to the conventionally fabricated side of the molten steel for meeting said components system Method is by reheating slab, hot rolling, hot-roll annealing, pickling etc. manufacture.
For example, hot rolling can be carried out to slab under normal rolling temperature, and can be at 900 DEG C to 1200 DEG C to warp The steel plate of hot rolling carries out annealing 10 minutes to 60 minutes.Later, cold rolling can be carried out by the steel plate to hot rolling by conventional method To be made into thin plate.The low alloy steel plate that the intensity and ductility of an embodiment according to the present invention are excellent can be such as In the common product of molding using and may be used as band, bar, plate, sheet material, pipeline or pipe.
It hereinafter, will the present invention will be described in detail referring to following embodiment.However, following embodiment is intended to more in detail Carefully illustrate the present invention, but the scope of the present invention is not limited to these embodiments.
Embodiment
Prepare the sample of steel corresponding with the compositing range of composition according to the present invention, and in hot rolling and hot-roll annealing Phase fraction, elongation percentage and the tensile strength of material are measured later.Table 1 below illustrates the composition of alloy of experiment steel type (weights Measure %).
[table 1]
Classification C Si Mn Cr Cu N Ni Mo Al Sn
Steel 1 of the invention 0.078 1.98 10.3 14.1 2.05 0.134 0 0.100 - -
Steel 2 of the invention 0.080 2.02 8.2 13.9 2.03 0.144 0 0 - -
Steel 3 of the invention 0.080 1.03 8.9 13.9 2.00 0.157 0.100 0.1 - -
Steel 4 of the invention 0.078 1.00 9.0 14.1 1.00 0.149 0.060 0.1 - -
Steel 5 of the invention 0.079 2.01 9.0 14.0 0.51 0.146 0.120 0 - -
Steel 6 of the invention 0.12 1.79 9.8 14.4 2.0 0.14 0.100 0 0.11 0.003
Steel 7 of the invention 0.082 2.36 11.8 15.3 2.48 0.133 0.100 0.1 - -
Steel 8 of the invention 0.082 0.198 9.7 14.1 2.00 0.140 0.050 0.05 - -
Steel 9 of the invention 0.077 2.05 10.3 13.4 1.98 0.160 0.100 0.1 - -
Steel 10 of the invention 0.21 1.99 10 14.0 2 0.145 0.1 0 0.002 0.003
Steel 11 of the invention 0.1 1.23 9.2 14.1 2.03 0.167 0 0 0.2 0.04
Compare steel 1 0.086 2.01 4.1 15.9 2.02 0.140 0 0 - -
Compare steel 2 0.085 0.197 4.1 15.8 1.96 0.130 0.100 0.06 - -
Compare steel 3 0.071 2.04 4.0 15.9 0.27 0.210 0.120 0 - -
Compare steel 4 0.087 0.200 6.0 17.9 2.00 0.180 0 0
Compare steel 5 0.019 1.88 10.0 14.1 0.82 0.066 0 0 0.002 0.003
To by carrying out the heat obtained and hot rolling to forming the material for preparing like that as described above under common rolling temperature Rolled steel plate carries out hot-roll annealing, to evaluate microscopic structure and phase fraction and relevant intensity and elongation percentage.
Fig. 1 to Fig. 4 is to show the photo of steel and the hot-workability for comparing steel of the invention.Fig. 1 shows of the invention Steel 8, Fig. 2 shows steel 9 of the invention, and Fig. 3 shows steel 11 of the invention.Referring to figs. 1 to Fig. 3, it is well established that this hair Bright steel shows the tissue of a part of austenite one phase or martensite after cooling, so that in hot rolling almost without edge Cracking.Steel 11 of the invention (wherein some ferritic phases with 5% or less amount presence) in the case where, at some edges Place cracks, but this is not a problem.However, in the case where comparing steel 4 shown in Fig. 4, there are considerable amount of ferrite, This leads to serious cracking during hot rolling, to throw into question in hot rolling.
On the other hand, hot rolling is carried out to material produced under normal rolling temperature.To the hot rolled steel plate prepared into Row hot-roll annealing, to determine microscopic structure and phase fraction as shown in following table 2.Hot-roll annealing is carried out about at 1100 DEG C After 30 minutes, it is cooling to carry out water, and observe tissue under an optical microscope.Phase point is measured by using ferrite range Number.Observation as optical microscopy is as a result, when there are martensitic phase, by using image analyzer and ferrite range number According to being compared to separation ferrite fraction and martensite fractions.
[table 2]
Referring to table 2, it can be seen that in most of steel in steel of the invention, discrete phase is austenite phase, and remaining Tissue slightly changes according to component system, but keeps ferrite or martensitic phase.In addition, it is well established that residual quantity be 5% or It is smaller.However, in the case where the comparison steel of serious crack at edge occurs during hot rolling, find most of steel be by austenite and The two-phase structure of ferritic phase composition.Particularly, in the case where relatively steel 5, after hot-roll annealing most of microscopic structure from Austenite is changed into martensitic phase, and a part of microscopic structure of heat is left retained austenite phase.It is well established that existing suitable The elongated ferritic phase along rolling direction of amount.In the case where steel of the invention is in annealing region, it is well established that Other than the presence of the difference of crystal grain and some ferritic phases or martensitic phase, microscopic structure is almost without difference.
Fig. 5 to 10 is to show to be heat-treated 30 minutes at a temperature of 1100 DEG C of hot-roll annealing, the sheet being then cooled directly with water The light micrograph of the steel of invention and the tissue for comparing steel.
Fig. 5 is to show the photo of the microscopic structure of steel 2 of the invention, wherein observes austenite phase and remaining geneva Body phase.
Fig. 6 is to show the photo of the microscopic structure of steel 8 of the invention, wherein observes austenite phase and remainder fe element Body phase.
Fig. 7 is to show the photo of the microscopic structure of steel 9 of the invention, wherein only observes austenite phase.
Fig. 8 is to show the photo for the microscopic structure for comparing steel 1, wherein observes the iron element extended in the rolling direction Body phase and austenite phase.
Fig. 9 is to show the photo for the microscopic structure for comparing steel 4, wherein observes austenite phase and ferritic phase.
Figure 10 is to show the photo for the microscopic structure for comparing steel 5, wherein observe ferritic phase and martensitic phase and Austenite phase.
Fig. 5 to Figure 10 corresponds to the representative microstructure picture of table 2.It is ensured that the measurement result in table 2 It is actually consistent with observation result of the Fig. 5 into Figure 10.
On the other hand, Figure 11 to Figure 14 be show sample for the alloy compositing range with steel 9 of the invention and The photo that the microscopic structure of speech changes according to 900 DEG C to 1200 DEG C of hot-roll annealing temperature.
Even if when hot-roll annealing temperature rises to 900 DEG C or higher, grain coarsening, but it has been found that, it can be ensured that foot Enough ideal tissues.
Figure 15 is the steel of the invention for showing an embodiment according to the present invention and the tension test knot for comparing steel The figure of fruit.
Referring to Fig.1 5, in the case where steel of the invention, elongation percentage percentage is greater than 40%, and tensile strength is 650MPa or higher.In addition, when material deforms or when by stress, the value of load-deformation curve and tensile strength is according to main phase, Austria Change to the deformational behavior of family name's body phase and big degree.In steel 5 and 8 of the invention, (wherein, strain inducing martensite transfor mation is well Occur) in, elongation percentage may insure not less than 40%, and tensile strength is 1200MPa, this shows to may insure high intensity.
Although the disclosure has been described in detail referring to exemplary implementation scheme, it will be understood by those skilled in the art that It is without departing from the spirit and scope of the disclosure, various changes can be carried out in terms of form and details.
Industrial applicibility
The excellent low alloy steel plate of the intensity and ductility of an embodiment according to the present invention be Cr-Mn austenite not Become rusty steel, and Cr-Mn austenitic stainless steel eliminates Ni and has excellent physical property and can be applied to various structural woods Material field, such as vehicle structure steel plate.

Claims (5)

1. a kind of intensity and the excellent low alloy steel plate of ductility, the low alloy steel plate includes with the weight percent of total composition (%) meter: 0.05% to 0.3% carbon (C), 0.7% to 2.5% silicon (Si), 8% to 12% manganese (Mn), 13% to 15.5% chromium (Cr), 0.5% to 3.0% copper (Cu), 0.1% to 0.2% nitrogen (N), 0.25% or less aluminium (Al), 0.25% or less tin (Sn), and rest part is iron (Fe) and other inevitable impurity,
Wherein, it is 5% or less ferritic phase and martensitic phase that the microscopic structure of the low alloy steel plate, which includes volume fraction, At least one of, and rest part includes austenite phase.
2. low alloy steel plate according to claim 1 also includes 0.2% or less nickel (Ni).
3. low alloy steel plate according to claim 1 or 2 also includes 0.2% or less molybdenum (Mo).
4. low alloy steel plate according to claim 1, wherein the elongation percentage of the low alloy steel plate is 40% or bigger.
5. low alloy steel plate according to claim 1, wherein the tensile strength of the low alloy steel plate is for 650MPa or more Greatly.
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