CN109266959A - The excellent cryogenic steel of surface processing quality - Google Patents
The excellent cryogenic steel of surface processing quality Download PDFInfo
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- CN109266959A CN109266959A CN201811116893.0A CN201811116893A CN109266959A CN 109266959 A CN109266959 A CN 109266959A CN 201811116893 A CN201811116893 A CN 201811116893A CN 109266959 A CN109266959 A CN 109266959A
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- steel
- weight
- cryogenic steel
- austenite
- surface processing
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 105
- 239000010959 steel Substances 0.000 title claims abstract description 105
- 238000012545 processing Methods 0.000 title claims abstract description 31
- 229910001566 austenite Inorganic materials 0.000 claims description 54
- 239000011572 manganese Substances 0.000 claims description 47
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 45
- 229910052799 carbon Inorganic materials 0.000 claims description 37
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 34
- 229910052748 manganese Inorganic materials 0.000 claims description 25
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 23
- 239000011651 chromium Substances 0.000 claims description 21
- 229910052759 nickel Inorganic materials 0.000 claims description 21
- 229910052804 chromium Inorganic materials 0.000 claims description 17
- 239000010949 copper Substances 0.000 claims description 15
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 14
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 13
- 230000014509 gene expression Effects 0.000 claims description 11
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 9
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 8
- 239000004411 aluminium Substances 0.000 claims description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 235000016768 molybdenum Nutrition 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 abstract description 11
- 238000003860 storage Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 description 17
- 229910000734 martensite Inorganic materials 0.000 description 13
- 230000015572 biosynthetic process Effects 0.000 description 9
- 238000005516 engineering process Methods 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 239000000203 mixture Substances 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 8
- 239000004576 sand Substances 0.000 description 8
- 230000006641 stabilisation Effects 0.000 description 8
- 238000011105 stabilization Methods 0.000 description 8
- 239000004615 ingredient Substances 0.000 description 7
- 230000009467 reduction Effects 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 230000002159 abnormal effect Effects 0.000 description 6
- 238000001816 cooling Methods 0.000 description 6
- 230000002829 reductive effect Effects 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 210000001519 tissue Anatomy 0.000 description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 230000000704 physical effect Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 230000002401 inhibitory effect Effects 0.000 description 3
- 230000036961 partial effect Effects 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 230000001737 promoting effect Effects 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 2
- ZLMJMSJWJFRBEC-UHFFFAOYSA-N Potassium Chemical compound [K] ZLMJMSJWJFRBEC-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 239000010962 carbon steel Substances 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000006731 degradation reaction Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 229910052700 potassium Inorganic materials 0.000 description 2
- 239000011591 potassium Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 150000001722 carbon compounds Chemical class 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 239000003949 liquefied natural gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 210000004872 soft tissue Anatomy 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C22C38/02—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
- C22C38/20—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
- C22C38/18—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
- C22C38/38—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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Coating With Molten Metal (AREA)
Abstract
The present invention relates to a kind of cryogenic steel that can be used at the low extensive temperature warmed to room temperature of liquefied gas storage and transporting equipment etc., after providing the stretched equal manufacturing procedure of one kind, also still with the cryogenic steel and its manufacturing method of excellent surface processing quality.
Description
This application claims preferential on December 25th, 2013 South Korea patent application submitted the 10-2013-0163369th
Power；The application is the Chinese patent application submitted the 201480070844.1st divisional application on December 19th, 2014.
Technical field
The present invention relates to a kind of cryogenic steel that surface processing quality is excellent, and in more detail, being related to one kind can liquefy
It is used at the low extensive temperature warmed to room temperature of gas storage tank and transporting equipment etc., and having excellent surface quality after processing is low
Temperature steel.
Background technique
Steel for the storage container of liquefied natural gas and liquid nitrogen etc., marine structure and arctic regions works should be
The cryogenic steel of sufficient toughness and intensity is also able to maintain that under ultralow temperature.This cryogenic steel will not only have the low of brilliance
Warm toughness and intensity, and the coefficient of thermal expansion and pyroconductivity for needing to have small, and be a kind of steel for being also contemplated that magnetic characteristic.
As material workable in a low temperature of liquefied gas environment, in the prior art using the Cr-Ni of AISI304 etc.
The aluminium alloy etc. of class stainless steel or 9%Ni steel and 5000 series.However, the Master Cost of aluminium alloy is high, and due to low strong
It spends and increases the design thickness of works, and welding procedure is also poor, so that its use is restricted.On the other hand, Cr-
The nickel containing high price such as Ni class stainless steel and 9%Ni steel, and additional heat treatment is needed, to not only will increase manufacturing expenses
With, and welding material also contains the nickel of a large amount of high price, so that there are problems aspect is widely used.
In order to solve these problems, the technology as the nickel content for reducing high price by addition manganese, chromium etc., can enumerate
Such as patent document 1 (KR published patent the 1998-0058369th) and (the published International patent WO2007- of patent document 2
No. 080646).The patent document 1 be it is a kind of nickel content is reduced to 1.5~4%, and the manganese of addition 16~22%, 2 respectively
~5.5% chromium ensures austenite structure, to improve the technology of pole low-temperature flexibility, and patent document 2 is a kind of by nickel
Content is reduced to 5.5% degree, and the manganese below of addition 2.0%, 1.5% chromium below respectively, and by heat treatment repeatedly and
Tempering, miniaturize ferrite crystal grain, so that it is guaranteed that the technology of pole low-temperature flexibility.However, the patent document 1 and 2 is also still
Nickel containing high price, and in order to ensure pole low-temperature flexibility, implements the heat treatment repeatedly and tempering of multiple steps, therefore, to taking
It is unfavorable in terms of simplification with aspect or process.
As another technology of structural steel used in liquefied gas is related to, can enumerate as exclude completely nickel, it is so-called
Without nickel (Ni-free) potassium steel.The potassium steel is divided into ferrite type and austenitic type according to the additive amount of manganese.For example, specially
Sharp document 3 (US granted patent the 4257808th) is a kind of manganese for replacing 9% nickel addition 5%, and in austenite and ferrite
The two-phase section temperature range coexisted, by being heat-treated repeatedly to it 4 times, thus be tempered after miniaturizeing crystal grain, from
And improve the technology of pole low-temperature flexibility.In addition, patent document 4 (KR published patent the 1997-0043149th) is a kind of addition
13% manganese, and in austenite and ferritic two-phase section temperature range, by being heat-treated repeatedly to it 4 times, to make
After crystal grain miniaturization, it is tempered, to improve the technology of pole low-temperature flexibility.In the patent document 3 and 4, ferrite is
Main Tissues, and in order to obtain pole low-temperature flexibility, by 4 times or more heat treatment repeatedly and tempering, to keep ferrite brilliant
Grain miniaturization, and using this as purport.However, for this technology, due to being heat-treated the increase of number, to expense can be made to increase
The problem of adding, also having Equipment for Heating Processing load.Therefore, develop it is a kind of for obtaining the technology of ultralow-temperature flexibility, described
In technology, not using ferrite as Main Tissues, but austenite (or austenite and ε-martensite line and staff control) is made
For Main Tissues.
In the case where using austenite as the cryogenic steel of Main Tissues, although can be made by adding a large amount of carbon and manganese
Stabilization of austenite, still, this can have an impact the recrystallization behavior of austenite, thus in conventional rolling temperature section,
Since partial, re-crystallization and uneven grain are grown, it can only make the austenite grain undue growth of specific minority, to can lead
The serious unevenness of austenite grain size in microstructure is caused to homogenize.
Summary of the invention
Technical problems to be solved
The present invention is intended to provide a kind of after the processing of drawing and bending etc., also still has excellent surface processing quality
Cryogenic steel.
Technological means
The present invention realizes that the cryogenic steel includes 15~35 by a kind of cryogenic steel that surface processing quality is excellent
The manganese (Mn) of weight %, the carbon (C) for meeting 23.6C+Mn >=28 and the condition and range of 33.5C-Mn≤23, more than 0 weight % to 5 weights
Amount % copper below (Cu), more than 0 weight % to 1 weight % nitrogen below (N), meet the condition and range of 28.5C+4.4Cr≤57
Chromium (Cr) and 5 weight % nickel below (Ni), 4 weight % silicon below (Si) and 5 weight % aluminium below (Al) in one
Kind or more, the iron (Fe) and other inevitable impurity of surplus.
Beneficial effect
The present invention can provide a kind of steel that surface processing quality is excellent, the steel by adjust the compositions of steel at
Point and compositing range improve stacking fault energy (Stacking Fault Energy), to even if be formed inside steel different
Often coarse crystal grain also still has excellent surface processing quality.
Detailed description of the invention
Fig. 1 is austenite grain coarsening, to form the shooting of the microstructure of the existing steel of abnormal coarse grain
Photo.
The non-uniform photo in surface captured after the existing steel that Fig. 2 is drawing Fig. 1, to show steel.
Fig. 3 is austenite grain coarsening, to form the micro- of the steel of one embodiment of the invention of abnormal coarse grain
The shooting photo carefully organized.
Fig. 4 be one embodiment of the invention of drawing Fig. 3 steel after captured, the uniform photo that shows surface.
Fig. 5 is the chart for showing the range of the carbon and manganese that control in the present invention.
Preferred forms
The present invention relates to a kind of after the manufacturing procedure of drawing and bending etc., also still processes with excellent surface
The cryogenic steel and its manufacturing method of quality, moreover, it is unrelated with abnormal coarse crystal grain is formed inside steel.
In general, the deformational behavior of carbon and the high austenite structure of manganese content is different from general carbon steel, by sliding and
Twin realizes, although also, deformation initial stage mainly realized by the sliding as homogeneous deformation, later can be adjoint
There is the twin as inhomogeneous deformation.The key variables of stress needed for generating twin are, the function of added element
Stacking fault energy and grain size can be such that stress needed for twin formation reduces in particular, grain size is bigger, thus even if
Under slight deformation, it is also easy to produce twin.When a small number of coarse crystal grain is present in microstructure, deformation initial stage exists
Twin deformation can be generated in coarse grain, so as to cause inhomogeneous deformation, therefore, the surface characteristic of material can be made to be deteriorated, thus
Induce the in uneven thickness of final structure object.Especially as low-temperature pressure container, need by ensuring that uniform steel are thick
In the case where spending the works to realize resistance to pressure, it can be led to the problem of in structure design and use big.Therefore, pass through addition
In the case where the steel of carbon and Meng Laishi microstructure austenitizing, institute can be deformed by solving the early stage twin of coarse grain
Unevenly improve surface processing quality in caused surface.
Therefore, the steel largely containing carbon and manganese can cause the part of austenite structure again in conventional rolling temperature region
Crystallization and crystal grain-growth, so that abnormal coarse austenite can be generated.In general, when critical stress ratio needed for forming twin slides
Want high, still, in the case where causing crystal grain big for these reasons, stress needed for forming twin will be reduced, thus becoming
Shape initial stage can generate twin deformation, therefore, the deterioration of surface quality can occur because of discontinuous deformation.The present invention is generating exception
In the case where coarse austenite grain, deformation twins can also be inhibited by limit stress needed for improving twin deformation
It generates.
In the following, the cryogenic steel excellent to surface processing quality of the invention is described in detail.
The excellent cryogenic steel of surface processing quality of the invention includes the manganese (Mn) of 15~35 weight %, meets 23.6C+
The carbon (C) of Mn >=28 and the condition and range of 33.5C-Mn≤23, more than 0 weight % to 5 weight % copper below (Cu), more than 0 weight
Measure % to 1 weight % nitrogen below (N), meet the chromium (Cr) and 5 weight % nickel below of the condition and range of 28.5C+4.4Cr≤57
(Ni), one or more of 4 weight % silicon below (Si) and 5 weight % aluminium below (Al), the iron (Fe) of surplus and other
Inevitable impurity.
Also, the stacking fault energy (SFE) of cryogenic steel of the invention calculated according to following relational expressions 1 should be 24mJ/
m2More than:
[relational expression 1]
SFE(mJ/m2)=1.6Ni-1.3Mn+0.06Mn2-1.7Cr+0.01Cr2+15Mo-5.6Si+1.6Cu+5.5Al-
60(C+1.2N)1/2+26.3(C+1.2N)(Cr+Mn+Mo)1/2+0.6[Ni(Cr+Mn)]1/2,
[wherein, the weight % that Mn, C, Cr, Si, Al, Ni, Mo and N of each numerical expression indicate each component content].
The high steel of manganese content are compared with general carbon steel, since stacking fault energy is low, are easy to generate the position of part
Wrong (dislocations), also, due to this highdensity partial dislocation, it will lead to deformation of steel behavior and generate variation.Cause
This, can make the deformational behavior of steel generate variation, and this stacking fault energy is as conjunction by control stacking fault energy
The function of gold element, the degree for increasing or decreasing energy value according to each element are different.The formula 1 is the alloy shown according to addition
The relational expression of the variation of the stacking fault energy of the content of element is the various realities of the calculated value and the present inventor by existing theory
It tests and calculated relational expression.
Fig. 3 shows fine group of the steel of the one embodiment of the invention of condition for meeting the ingredient compositing range and formula 1
The shooting photo knitted, Fig. 1 show the shooting photo of the microstructure of existing steel.It can be confirmed from Fig. 1 and Fig. 3 fine
Organize the formation of abnormal coarse crystal grain.
Fig. 2 is the steel surface that drawing is as existing steel, captured after the steel of microstructure with Fig. 1
Photo can be confirmed and have occurred unevenly.However, if fine group with Fig. 3 to drawing as an embodiment of the present invention
When Fig. 4 of captured steel surface is confirmed after the steel knitted, even if it is abnormal coarse then to can be confirmed that microstructure is formed with
Crystal grain, it is also uneven without generating, it is different from Fig. 2.
[relational expression 2]
It can be illustrated by the formula 2, as shown in Fig. 2 of one embodiment of the invention, the surface after processing is still uniform.When
When steel are deformed from outside by external force, caused to slide by moving for dislocation, while Austria high in carbon and manganese content
It in the case where family name's body steel, is further deformed along with twin due to low stacking fault energy, thus at deformation initial stage, mainly
The deformation caused by sliding occurs, still, later, when more than limit stress needed for generating twin, twin will occur simultaneously
Deformation.In general, the sliding deformation as caused by dislocation is on the other hand homogeneous deformation is deformed into uneven change as caused by twin
Shape, in particular, the part coarse grain being confined in steel and occur twin deformation when, after deformation can along with microstructure not
Uniformly, thus in the use of steel not preferably.
In general, critical stress ratio needed for generating twin wants high when sliding, still, it has been confirmed that if crystal grain from formula 2
Size become thick, then the stress for generating twin can reduce, therefore, formed twin needed for stress reduce, to will lead to
Deformation initial stage locally generates twin in coarse crystal grain, and the deterioration of surface quality thus can be caused because of discontinuous deformation.
However, it is found that can improve twin by improving stacking fault energy generates stress, and and crystal grain from formula 2
Size it is unrelated, it is therefore, unrelated with coarse crystal grain is formed, excellent surface quality can also be obtained after processing.
By the way that the stacking fault calculated according to the formula 1 to be able to maintain more than a certain size, so as to inhibit twin
It generates, also, the composition by keeping the steel of the stacking fault energy more than a certain size, it is excellent so as to provide surface quality
Different cryogenic steel.
In the following, being illustrated to the restriction reason respectively formed for limiting steel.
Manganese (Mn): 15~35 weight %
Manganese is to play the role of the element for making stabilization of austenite in the present invention.In the present invention, in order to make extremely low temperature
Under austenite phase stabilize, preferably comprise the Mn of 15 weight % or more.That is, when the content of manganese is less than 15 weight %, if
Carbon content is few, then forms ε-martensite of metastable phase, and be readily converted into α-due to the strain-induced transformation under extremely low temperature
Martensite, therefore be unable to ensure toughness, also, in order to prevent these, when attempting to stablize austenite by increasing carbon content
When change, physical property rapid degradation can be made because of the precipitation of carbide instead, therefore not preferably.Therefore, the content of manganese is preferably
15 weight % or more.On the other hand, when the content of manganese is more than 35 weight %, the corrosion rate of steel can be made to reduce, and by
In the increase of content, can there are problems that economy reduction.It is therefore preferable that the content of the manganese is limited to 15~35 weights
Measure %.
Carbon (C): meet the condition of 23.6C+Mn >=28 and 33.5C-Mn≤23
Carbon is to make stabilization of austenite, increases the element of intensity, in particular, playing reduces MsAnd MdEffect, the MsAnd Md
For the transformation temperature for converting the austenite into ε martensite or alpha martensite because of cooling procedure or processing.Therefore, when the carbon of addition not
When abundant, since the stability of austenite is insufficient, so that stable austenite can not be obtained under ultralow temperature, in addition, due to outer
Portion's stress is easy strain-induced transformation to ε-martensite or alpha martensite, to reduce toughness, but also reduces the strong of steel
On the other hand degree when carbon content is excessive, can make toughness rapid degradation because of the precipitation of carbide, and can be because of the mistake of intensity
Degree increases and processability is made to be deteriorated.
Especially in the present invention, for carbon content, by paying attention to and the pass between carbon and other elements added together
Be and be determined as preferably, in order to these, by the inventors discovered that be shown in Fig. 5 in the carbon and the relationship of manganese formed in carbide
In.It is recognized that while carbide is formed due to carbon from attached drawing, still, the formation of carbide be more than independently by
The influence of carbon, but its formation is had an impact and the compound action with manganese.Carbon content appropriate is shown in figure.
The formation of carbide in order to prevent in the figure, other ingredients meet the present invention specified in range under the premise of, preferably will
The value of 23.6C+Mn (C, M are the content that each ingredient is indicated with weight %) is controlled 28 or more.It indicates the parallelogram of figure
The inclined left border in region.When 23.6C+Mn is less than described 28, the stability of austenite will be reduced, thus can be because extremely low
Temperature under impact and cause strain-induced transformation, to impact flexibility can be made to reduce.When carbon content is excessively high, that is, 33.5C-Mn
When greater than 23, Carbide Precipitation can be made because of the excessive addition of carbon and reduce low-temperature impact toughness.Therefore, in the present invention, excellent
Choosing addition meets the carbon (C) of the condition of 23.6C+Mn >=28 and 33.5C-Mn≤23.As can be known from Fig. 5, meeting the numerical expression
In the range of, the most lower limit value of C content is 0 weight %.
Copper (Cu): 5 weight % or less (except 0 weight %)
Solid solubility of the copper in carbide is very low, and slow in the intracorporal diffusion of Ovshinsky, therefore can be concentrated in and Ovshinsky
On the interface of the carbide of bodily form nucleation, it thus can effectively slow down the growth of carbide by obstruction Carbon diffusion, finally,
Have the effect of that carbide is inhibited to generate.For base material, in the fabrication process, carbide can be inhibited to analyse by accelerating cooling
Out, still, welding heat affected zone is not easily controlled cooling velocity, and therefore, addition in the present invention inhibits non-as to carbide
The often copper of effective element.In addition, copper has by making stabilization of austenite, to improve the effect of pole low-temperature flexibility.But
When the content of Cu is more than 5 weight %, can there are problems that reducing the hot-workability of steel, it is therefore preferable that by the upper limit value of Cu
It is limited to 5 weight %.The content of copper for obtaining above-mentioned carbide inhibitory effect is preferably 0.5 weight % or more.
Nitrogen (N): 1 weight % or less (except 0 weight %)
Nitrogen is to make stabilization of austenite together with carbon, so that the element of toughness is improved, in particular, being a kind of logical as carbon
Solution strengthening is crossed to improve the very favorable element of intensity aspect.In particular, it is found that being a kind of by effectively improving from formula 1
Stacking fault energy come promote sliding element.But when addition is more than 1% nitrogen, stress needed for generating twin will be more than phase
When the stress value of the processing capacity in conventional steel, thus it is unnecessary, also, due to forming coarse nitride, thus in the presence of
The problem of deteriorating the surface quality of steel and physical property, it is therefore preferable that upper limit value is limited to 1 weight %.
Other than above-mentioned element, austenite steel of the invention can also include Cr, Ni, Si, Al.
Chromium (Cr): 28.5C+4.4Cr≤57
For chromium in the amount of being properly added range, playing makes stabilization of austenite, thus the work of the impact flexibility under improving low temperature
With, and be solid-solution in austenite, to play the role of increasing the intensity of steel.In addition, chromium is also a kind of raising steel
Corrosion proof element.But chromium is as carbide formers, in particular, being a kind of in austenite grain boundary formation carbide, to reduce low
The element of temperature impact.Therefore, for the content of the chromium added in the present invention, by paying attention to and carbon and other elements added together
Between relationship and be determined as preferably, carbide is formed in order to prevent, meets range specified in the present invention in other ingredients
Under the premise of, preferably the value of 28.5C+4.4Cr (C, Cr are the content that each ingredient is indicated with weight % unit) is controlled below 57.
When the value of 28.5C+4.4Cr is more than 57, can be difficult to effectively inhibit in austenite grain boundary because of excessive chromium and carbon content
Therefore the generation of carbide can there are problems that making the impact flexibility under low temperature to reduce.Therefore, preferred addition in the present invention
Meet the chromium of 28.5C+4.4Cr≤57.
Nickel (Ni): 5 weight % or less
Nickel is effective austenite stabilizer element, and is that one kind plays reduction MsAnd MdEffect, to improve steel
Toughness element, the MsAnd MdTo convert the austenite into ε-martensite or alpha martensite because of cooling procedure or processing
Transformation temperature.In particular, it is found that nickel is a kind of element for promoting sliding by effectively improving stacking fault energy from formula 1.But
When adding nickel more than 5 weight %, stress needed for generating twin is by answering more than the processing capacity for being equivalent to conventional steel
Force value, thus it is unnecessary, and be the element of high price, therefore can there are problems that reducing economy, it is therefore preferable that by upper limit value
It is limited to 5 weight %.
Silicon (Si): 4 weight % or less
Silicon is a kind of element of castability for improving molten steel, when especially one kind is added in austenite steel, is solid-solution in
Inside steel, to effectively increase the element of intensity.But when addition is more than 4% silicon, stacking fault energy can be reduced, from
And promote the generation of twin, and the reduction of high intensity bring toughness can be caused, it is therefore preferable that upper limit value is limited to 4 weights
Measure %.
Aluminium (Al): 5 weight % or less
Aluminium is that one kind makes stabilization of austenite in the amount of being properly added range, and plays reduction MsAnd MdEffect, thus
Improve the element of the toughness of steel, the MsAnd MdTo convert the austenite into ε-martensite or α-because of cooling procedure or processing
The transformation temperature of martensite.In addition, it is that one kind is solid-solution in inside steel, thus increase the element of intensity, especially a kind of pair of steel
The mobility of interior carbon has an impact, and effectively inhibits the formation of carbide, to increase the element of toughness.In particular, from formula 1
It is found that being a kind of element for promoting sliding by effectively improving stacking fault energy.But when aluminium of the addition more than 5 weight %
When, stress needed for generating twin can be more than the stress value for being equivalent to the processing capacity of conventional steel, thus it is unnecessary, also,
By the formation of oxide and nitride, the castability of steel and surface quality can be made to be deteriorated, it is therefore preferable that upper limit value is limited to
5 weight %.
Also, austenite steel of the invention can also include Mo.
Molybdenum (Mo): 5 weight % or less
Molybdenum is that one kind makes stabilization of austenite in the amount of being properly added range, and plays reduction MsAnd MdEffect, thus
Improve the element of the toughness of steel, the MsAnd MdTo convert the austenite into ε-martensite or α-because of cooling procedure or processing
The transformation temperature of martensite.In addition, being that one kind is solid-solution in inside steel, to increase the element of intensity, especially one kind passes through inclined
It analyses in austenite grain boundary, to improve the stability of crystal boundary, and reduces energy, to play the crystal boundary analysis for inhibiting carbonitride
The element of effect out.In particular, it is found that being a kind of member for promoting sliding by effectively improving stacking fault energy from formula 1
Element.But when adding the molybdenum more than 5 weight %, stress needed for generating twin will be more than the processing for being equivalent to conventional steel
The stress value of amount, thus it is unnecessary, and too big effect is not had yet to crystal boundary stability.In addition, due to the member that molybdenum is high price
Element, therefore economy can be reduced, and the reduction of high intensity bring toughness can be caused, it is therefore preferable that upper limit value is limited to 5
Weight %.
Remaining ingredient of the invention is iron (Fe) and other inevitable impurity.But in common steel and iron manufacturing mistake
Cheng Zhong can inevitably be mixed into from raw material or ambient enviroment and be not intended to mixed impurity, therefore being mixed into for these impurity is
Inevitably.These impurity are well known for the technical staff of the iron steel making processes of this field routine, therefore
All the elements about impurity are not recorded in this specification especially.
For the cryogenic steel, in terms of area fraction, 95% or more austenite structure is preferably comprised.At low temperature
The representative soft tissue austenite of ductile failure is shown, as ensuring necessary to low-temperature flexibility fine group
It knits, in terms of area fraction, preferably comprises 95% or more, when being less than 95%, cannot ensure sufficient low-temperature flexibility, that is ,-
It is difficult to substantially ensure the impact flexibility of 41J or more at 196 DEG C, it is therefore preferable that the lower limit value is limited to 95%.
In terms of area fraction, carbide content present in the austenite grain boundary is preferably 5% or less.In the present invention
In, representative group may be present other than austenite is woven with carbide, on the Carbide Precipitation to austenite grain boundary, thus
The reason of as intercrystalline cracking, to make low-temperature flexibility and ductility be deteriorated, it is therefore preferable that the upper limit value is limited to 5%.
The opening for 5% elongation strain that the twin generation stress of the cryogenic steel is preferably correspond to the cryogenic steel is answered
It is more than power.Wherein, twin, which generates stress, indicates the value calculated according to formula 2, and elongation strain indicates that single shaft is drawn when stretching experiment
5% elongation strain has occurred when stretching.In general, when being formed to the plate for manufacturing the low temperature structures object such as low-temperature (low temperature) vessel,
When provided deflection is converted into elongation strain, most of is the level within 5%, therefore, for inhibiting inhomogeneous deformation
Twin generate stress be preferably limited to tensile stress when being uniaxially stretched corresponding to 5% deflection or more.
In the following, the manufacturing method of the cryogenic steel excellent to surface processing quality of the invention is described in detail.
The present invention the following steps are included: prepare steel ingot the step of, the steel ingot have aforementioned present invention steel composition, and
And according to above-mentioned relation formula 1 calculate stacking fault energy (SFE) be 24mJ/m2More than；1050~1250 DEG C at a temperature of plus
The step of hot steel ingot；And 700~950 DEG C at a temperature of, to it is described by heating steel ingot carry out finish rolling hot rolling
Step.
For cryogenic steel constructed in accordance, prepare there is composition of alloy above-mentioned and according to the relational expression first
1 stacking fault energy (SFE) calculated is 24mJ/m2Above steel ingot.
Then, the steel ingot is heated, and heating temperature is preferably 1050~1250 DEG C.Its steel that is used to be dissolved and homogenize
It the solid solution of the cast sturcture, segregation and the secondary phase that are generated in ingot manufacturing step and homogenizes, when heating temperature is lower than 1050 DEG C,
Since the temperature of homogenize deficiency or heating furnace is too low, to deformation drag when hot rolling can be made to increase, when more than 1250 DEG C
When, segregated zone of the meeting in cast sturcture causes the deterioration of partial melting and surface quality.Therefore, the reheating temperature of the steel ingot
Degree ranges preferably from 1050~1250 DEG C.
The hot rolling is preferably implemented under 700~950 DEG C of final rolling temperature, when the final rolling temperature is lower than 700 DEG C, carbon
Compound can be precipitate on austenite grain boundary, to make elongation and low-temperature flexibility reduce, in addition, since each of microstructure occurs
Anisotropy, so that the anisotropy of engineering properties can occur.When the final rolling temperature is more than 950 DEG C, austenite grain can be made
Coarsening, to make intensity and elongation reduce, therefore not preferably, therefore, the final rolling temperature ranges preferably from 700~950
℃。
Specific embodiment
Hereinafter, the present invention will be more specifically described by embodiment.But it is necessary to note that aftermentioned embodiment is only to use
In illustrating the present invention, to make more specificization of the invention, the interest field being not intended to limit the invention.
The steel ingot for the ingredient recorded in following table 1 will be met, after being manufactured by the manufacturing condition recorded in following table 2,
The area fraction of stacking fault energy, microstructure, yield strength and carbide is measured and shown, and is measured in following Table 3
And the physical property values of elongation and Charpy impact toughness etc. are shown.Surface in following Table 3 unevenly observes by the naked eye
The surfaces of steel and evaluated.
Table 1
Table 2
As shown in above-mentioned table 2, meets the example 1 to 8 of composition range and the formula 1 of the invention, obtain fine
The area fraction of austenite in tissue is controlled in 95% or more, and carbide is controlled in stable Austria less than 5%
Family name's body, therefore, excellent toughness can be obtained at extremely low temperatures by showing.
Table 3
In addition, by above-mentioned table 3 it has been confirmed that example 1 to 8, compared with comparative example 1 to 3, impact flexibility is obtained substantially
Degree improves.The reason for this is that by the carbon and other elements of addition proper content under relatively low manganese content range, to obtain
Stable austenite, in particular, when carbon content is high the formation of carbide can be inhibited by adding copper, therefore keep austenite steady
It is qualitative to be also improved.
In particular, in invention steel 1 to 8, according to formula 1, so that stacking fault is able to satisfy 24mJ/m2More than, so as to obtain
It obtains and the non-uniform excellent steel in surface is not present.On the other hand, it is known that the stacking fault of comparative example 1 to 3 can exceed that institute
The range of formula 1 is stated, thus even if obtaining excellent ultralow-temperature flexibility, but it is uneven that surface has occurred.
Furthermore it is possible to confirm that the carbon of comparative example 4 and 6 and the content of manganese do not meet composition range of the invention, thus cannot
Expected austenite area fraction is obtained, therefore makes the reduction of pole low-temperature flexibility, furthermore it is possible to know stacking fault energy in the present invention
In be not inconsistent yet box-like 1 range, so that it is uneven to produce surface.
It is known that comparative example 5 and 7 is unsatisfactory for the composition range controlled in the present invention, therefore poor impact toughness, especially
The carbide of excessive area fraction is generated, on austenite grain boundary due to excessively adding for carbon so as to cause impact flexibility change
Difference.
Comparative example 8 is unsatisfactory for composition range of the invention, therefore, even if stacking fault can exceed that 24mJ/m2Also it produces
Surface is uneven.It has been confirmed that be particularly due to final rolling temperature lower than control temperature, and because of the anisotropy of physical property and
High intensity, to make elongation and poor impact toughness.
As described above, exemplary embodiments of the invention have shown and described, but, those skilled in the art can carry out respectively
Kind deformation and other embodiments.This deformation and other embodiments consider and are included in interest field, to be no more than this
The purport and range of invention.
Claims (6)
1. a kind of cryogenic steel that surface processing quality is excellent, which is characterized in that the cryogenic steel includes 15~35 weight %
Manganese (Mn), meet 23.6C+Mn >=28 and the condition and range of 33.5C-Mn≤23 carbon (C), more than 0 weight % to 5 weight % with
Under copper (Cu), more than 0 weight % to 1 weight % nitrogen below (N), meet the chromium of the condition and range of 28.5C+4.4Cr≤57
(Cr) and one of 5 weight % nickel below (Ni), 4 weight % silicon below (Si) and 5 weight % aluminium below (Al) with
On, the iron (Fe) and other inevitable impurity of surplus.
2. the excellent cryogenic steel of surface processing quality according to claim 1, which is characterized in that the cryogenic steel is also
Include 5 weight % molybdenums below (Mo).
3. the excellent cryogenic steel of surface processing quality according to claim 1, which is characterized in that the cryogenic steel with
Area fraction meter includes 95% or more austenite structure.
4. the excellent cryogenic steel of surface processing quality according to claim 3, which is characterized in that in terms of area fraction,
Carbide present in the austenite grain boundary is 5% or less.
5. the excellent cryogenic steel of surface processing quality according to claim 1, which is characterized in that the cryogenic steel
Twin generation stress is the tensile stress corresponding to 5% elongation strain of the cryogenic steel or more.
6. the excellent cryogenic steel of surface processing quality according to claim 1, which is characterized in that the cryogenic steel
It is 24mJ/m according to the stacking fault energy (SFE) that following relational expressions 1 calculate2More than:
Relational expression 1:
SFE(mJ/m2)=1.6Ni-1.3Mn+0.06Mn2-1.7Cr+0.01Cr2+15Mo-5.6Si+1.6Cu+5.5Al-60(C+
1.2N)1/2+26.3(C+1.2N)(Cr+Mn+Mo)1/2+0.6[Ni(Cr+Mn)]1/2,
Wherein, Mn, C, Cr, Si, Al, Ni, Mo and N of each numerical expression indicate the weight % of each component content.
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| PCT/KR2014/012601 WO2015099363A1 (en) | 2013-12-25 | 2014-12-19 | Low-temperature ingot steel having excellent surface processing quality |
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| JP6645103B2 (en) * | 2014-10-22 | 2020-02-12 | 日本製鉄株式会社 | High Mn steel material and method for producing the same |
| JP6589535B2 (en) * | 2015-10-06 | 2019-10-16 | 日本製鉄株式会社 | Low temperature thick steel plate and method for producing the same |
| KR101714922B1 (en) * | 2015-12-18 | 2017-03-10 | 주식회사 포스코 | Wear resistnat steel plate having excellent toughness and internal properties and method for manufacturing thereof |
| WO2017111489A1 (en) * | 2015-12-22 | 2017-06-29 | 주식회사 포스코 | Austenitic steel material having excellent hydrogen-embrittlement resistance |
| WO2018104984A1 (en) * | 2016-12-08 | 2018-06-14 | Ｊｆｅスチール株式会社 | HIGH Mn STEEL SHEET AND PRODUCTION METHOD THEREFOR |
| KR101940874B1 (en) * | 2016-12-22 | 2019-01-21 | 주식회사 포스코 | High manganese steel with superior low temperature toughness and yield strength and method for manufacturing the same |
| KR101917473B1 (en) * | 2016-12-23 | 2018-11-09 | 주식회사 포스코 | Austenitic steel having excellent wear resistance and toughness and method for manufacturing thereof |
| CN110573642A (en) * | 2017-04-26 | 2019-12-13 | 杰富意钢铁株式会社 | High Mn steel and method for producing same |
| KR102109270B1 (en) | 2017-10-18 | 2020-05-12 | 주식회사 포스코 | Low temperature high manganese steel plate with excellent surface property and method for manufacturing the same |
| EP3722448B1 (en) * | 2017-12-07 | 2024-03-06 | JFE Steel Corporation | High-mn steel and method for manufacturing same |
| KR102020381B1 (en) * | 2017-12-22 | 2019-09-10 | 주식회사 포스코 | Steel having excellent wear resistnat properties and method for manufacturing the same |
| KR102367801B1 (en) * | 2018-02-07 | 2022-02-24 | 제이에프이 스틸 가부시키가이샤 | High Mn steel and manufacturing method thereof |
| KR102004654B1 (en) * | 2018-03-23 | 2019-07-26 | 서울과학기술대학교 산학협력단 | Aluminium-added austenitic lightweight high-maganese steel having superior cryogenic temperature toughness and manufacturing method thereof |
| WO2019240910A1 (en) * | 2018-06-14 | 2019-12-19 | The Nanosteel Company, Inc. | High strength steel alloys with ductility characteristics |
| EP3831973A4 (en) * | 2018-08-03 | 2021-07-21 | JFE Steel Corporation | High-mn steel and method for producing same |
| WO2020035917A1 (en) * | 2018-08-15 | 2020-02-20 | Ｊｆｅスチール株式会社 | Steel sheet and method for manufacturing same |
| KR102255827B1 (en) * | 2018-10-25 | 2021-05-26 | 주식회사 포스코 | Low-temperature austenitic high manganese steel having excellent surface quality and manufacturing method for the same |
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| CN114480980B (en) * | 2021-12-29 | 2023-09-08 | 中国铁路设计集团有限公司 | Chromium-copper alloyed weather-resistant twin induced plasticity steel and preparation method thereof |
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| CN103370434A (en) * | 2010-12-13 | 2013-10-23 | Posco公司 | Austenitic, lightweight, high-strength steel sheet of which the yield ratio and flexibility are outstanding and a production method therefor |
| WO2013100614A1 (en) * | 2011-12-27 | 2013-07-04 | 주식회사 포스코 | Austenitic steel having superior machinability and cryogenic temperature toughness in weld heat affected zones thereof and method for manufacturing same |
| CN104220617A (en) * | 2011-12-27 | 2014-12-17 | Posco公司 | Austenitic steel having superior machinability and cryogenic temperature toughness in weld heat affected zones thereof and method for manufacturing same |
Also Published As
| Publication number | Publication date |
|---|---|
| US20160319407A1 (en) | 2016-11-03 |
| CN109266959B (en) | 2022-05-24 |
| WO2015099363A8 (en) | 2015-09-17 |
| JP2017507249A (en) | 2017-03-16 |
| CN105849302A (en) | 2016-08-10 |
| KR101543916B1 (en) | 2015-08-11 |
| KR20150075315A (en) | 2015-07-03 |
| CN105849302B (en) | 2018-08-28 |
| EP3088555A1 (en) | 2016-11-02 |
| JP6615773B2 (en) | 2019-12-04 |
| WO2015099363A1 (en) | 2015-07-02 |
| EP3088555A4 (en) | 2017-04-05 |
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