CN106574351A - High strength austenitic stainless steel and production method thereof - Google Patents
High strength austenitic stainless steel and production method thereof Download PDFInfo
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- CN106574351A CN106574351A CN201580044801.0A CN201580044801A CN106574351A CN 106574351 A CN106574351 A CN 106574351A CN 201580044801 A CN201580044801 A CN 201580044801A CN 106574351 A CN106574351 A CN 106574351A
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 title abstract description 6
- 239000010955 niobium Substances 0.000 claims abstract description 58
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 34
- 239000010936 titanium Substances 0.000 claims abstract description 33
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 28
- 238000000137 annealing Methods 0.000 claims abstract description 27
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 25
- 239000010959 steel Substances 0.000 claims abstract description 25
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 18
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 12
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 12
- 238000005096 rolling process Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract 3
- 238000000034 method Methods 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims 2
- 239000011733 molybdenum Substances 0.000 claims 2
- 229910052759 nickel Inorganic materials 0.000 abstract description 9
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910045601 alloy Inorganic materials 0.000 description 22
- 239000000956 alloy Substances 0.000 description 22
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical group [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 16
- 229910001566 austenite Inorganic materials 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 150000004767 nitrides Chemical class 0.000 description 6
- 238000005275 alloying Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000002360 preparation method Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 239000010935 stainless steel Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 229910001257 Nb alloy Inorganic materials 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000011020 pilot scale process Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 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
- 238000005469 granulation Methods 0.000 description 1
- 230000003179 granulation Effects 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- 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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—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
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- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Materials Engineering (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention relates to an austenitic stainless steel. The steel contains in weight % 0-0.4 % C, 0-3 % Si, 3-20 % Mn, 10-30 % Cr, 0-4.5 % Ni, 0-3 % Mo, 0-3 % Cu, 0.05-0.5 % N, 0-0.5 % Nb, 0-0.5 % Ti, 0-0.5 % V, the balance of Fe and inevitable impurities. The content of at least one of the elements in the group of niobium (Nb), titanium (Ti) or vanadium (V) is more than 0.05 % so that the total amount of the niobium (Nb), titanium (Ti) and vanadium (V) contents is at the range of 0.05 - 0.5 % for having the grain size of lower than 10 micrometer after annealing of the cold deformed product and the difference between the yield strengths of the steel measured in transverse and parallel directions to the rolling direction is lower than 5 %. The invention also relates to a method for producing such an austenitic stainless steel.
Description
The present invention relates to show the high-strength of the highly isotropic of the good combination and mechanical property of intensity and elongation percentage
Degree austenitic stainless steel.The invention further relates to the preparation method of the steel.
The yield strength of the austenitic stainless steel under annealed condition is relatively low.For increasing bending for austenic stainless steel belt material
The conventional method for taking intensity is smooth, i.e., strengthen the steel band by cold rolling.However, smooth with important inferior position：Jing puts down
The mechanical property of whole steel is tended to as high anisotropy.For example, the yield strength of flattened austenitic stainless steel exists
Transversely than the parallel direction in rolling direction up to many 20%.Anisotropy is shortcoming, for example, make the austenitic stainless steel
Shaping it is more difficult.
Additionally, smooth to sacrifice elongation percentage as cost increasing intensity.For some austenite stainless grades of steel, flattening process
Remaining elongation percentage and formability can be too low afterwards.
The refinement of the crystallite dimension of steel is to increase the well-known and effective method of the yield strength of austenitic stainless steel.
Substitute using the method smooth.According to well-known Hal l-Petch relations, the yield strength of the steel is with reduction
Crystallite dimension and increase.The refinement of crystallite dimension also has advantage compared with smooth：The anisotropy of mechanical property is significantly lower.
However, the preparation of the steel of fine grain granulation is difficult, because grain growth is very fast in its starting stage, and therefore process window
Mouthful (i.e. for reach admissible time and the temperature range of certain little crystallite size and intensity level) can be too little.If
The process window is too little, then mechanical property is too big along the steel band alterable.In the situation that can not reach target mechanical property
Under, may occur in which significant surrender loss.
It is well known that crystal grain life can usually be limited by adding the unit to form carbide and nitride to austenitic stainless steel
It is long.These elements form carbide and nitride, due to so-called Zener pinning effects, its limit grain growth.For example, JP
Disclose 2010215953 and disclose the austenitic stainless steel comprising niobium (Nb), titanium (Ti) or vanadium (V).However, the shortcoming of this steel
It is nickel which includes at least 4.5 weight %.JP discloses 2014001422 and is related to austenite stainless steel plate material (to be had in parent phase
10 μm or less of average crystalline crystallite dimension) and its manufacture method, the steel is in terms of weight % comprising C:0.02 to 0.30%,
Cr:10.0 to 25.0%, Ni:3.5 to 10.0%, Si:3.0% or less, Mn:0.5% to 5.0%, N:0.10 to 0.40%,
C+3×N:0.4% or more, and Fe and impurity are surplus, and also optionally include Mo:<3%, Cu:<3%, Nb:<
0.5%, Ti:<0.1% and V:<1% causes the summation of Nb+Ti+V to be 0-1.6%.2014001422 are disclosed according to this JP, when
During using Nb, Ti and V as alloying constituents, scope of the nickel content in 5.0-6.6 weight %.Due to nickel valency that is high and fluctuating
Lattice, such austenitic stainless steel are not have cost-efficient enough.For more there is cost-efficient low nickel high intensity austenite
There is the market demand in rustless steel.
The purpose of the present invention be prevent the shortcoming of prior art and preparation show little crystallite size, high intensity and it is each to
Same sex mechanical property has a cost-efficient high intensity austenitic stainless steel.The invention further relates to the processing method of the steel, and
With forming the element of carbide and nitride by the steel alloying, so as to limit grain growth and thus improve the steel plus
Work.The basic feature of the present invention is arranged in the appended claims.
According to the present invention, use and element such as niobium (Nb), titanium (Ti) and the vanadium (V) of carbide and nitride are formed to austenite
Rustless steel carries out alloying.For these elements effectively limit grain growth of carbide and nitride precipitate.Therefore, exist
In order to prepare the lehr attendant carried out for the fine grain size of cold deformation product by made by the austenitic stainless steel of the present invention
During skill, the presence of these Carbide Precipitation things and nitride precipitate causes larger process window and machinability to become can
Energy.In order to provide sufficiently strong effect, should add in the group more than the niobium (Nb), titanium (Ti) or vanadium (V) of 0.05 weight % extremely
A kind of few element.In order to the total amount for keeping austenitic stainless steel to have cost efficiency, niobium (Nb), titanium (Ti) and vanadium (V) is less than 0.5 weight
Amount %.
Austenitic stainless steel of the invention is made by the reduction of the nickel content compared with conventional nickel austenite stainless steel
There is cost efficiency.Therefore, nickel of the ladle of the invention containing no more than 4.5 weight %.
The rustless steel of the present invention is austenitic stainless steel, Si, 3- of its C, 0-3% comprising 0-0.4% in terms of weight %
N, 0-0.5% of Cu, 0.05-0.5% of Mo, 0-3% of Ni, 0-0.5% of Cr, 0-4.5% of 20% Mn, 10-30%
Nb, 0-0.5% Ti, 0-0.5% V, the total amount of niobium (Nb) content, titanium (Ti) content and vanadium (V) content is in 0.05-
0.5% scope causes the content of at least one element in the group of niobium (Nb), titanium (Ti) or vanadium (V) more than 0.05%, surplus
For Fe and inevitable impurity, such as phosphorus, sulfur and oxygen.In order to ensure required mechanical property, for cold deformation product and
Speech crystallite dimension after anneal is less than 10 microns, preferably smaller than 7 microns, and more preferably less than 5 microns.In rolling direction
Horizontal and parallel direction on difference between the stainless yield strength that measures be less than 5%.
High intensity austenitic stainless steel of the invention is prepared via conventional stainless steel art route, especially including molten
Change, AOD (aod) converters and Ladle Treatment, continuous casting, hot rolling, cold rolling, annealing and pickling.However, the temperature less than 1050 DEG C
Austenitic stainless steel of the invention is annealed by degree (temperature is less than the temperature in conventional fabrication process).The drop of annealing temperature
It is low to slow down grain growth, and thus it is capable of achieving less crystallite dimension and higher yield strength.However, in order to avoid having
Harmful sensitization phenomenon, the annealing temperature should be higher than that 700 DEG C.Required annealing region thus be 700-1050 DEG C, and move back
The fiery time be the 1-400 seconds, the preferred 1-200 seconds.Cold deformation drafts (such as cold roling reduction) should before annealing process
Sufficiently high to fine grain size can be formed.Deformation drafts degree such as cold roling reduction degree should be at least 50%.
The present invention is described more fully with reference to the following drawings, wherein
Fig. 1 shows the impact of annealing time and temperature to the crystallite dimension of the reference alloy not comprising niobium,
Fig. 2 shows the crystallite dimension of annealing time and temperature to the beta alloy of the invention comprising 0.05% niobium
Impact,
Fig. 3 shows the crystallite dimension of annealing time and temperature to the beta alloy of the invention comprising 0.11% niobium
Impact,
Fig. 4 shows the crystallite dimension of annealing time and temperature to the beta alloy of the invention comprising 0.28% niobium
Impact,
Fig. 5 shows the crystallite dimension of annealing time and temperature to the beta alloy of the invention comprising 0.45% niobium
Impact, and
Fig. 6 shows the combination of annealing window, i.e. annealing time and temperature, corresponding to not comprising niobium and include 0.11%
2-3 micron (μm) crystallite dimensions are reached in the beta alloy of niobium.
Have studied with different amounts of niobium five kinds of austenite beta alloy 1-5.Beta alloy displayed in Table 1
Chemical composition.
The chemical composition of 1 beta alloy 1-5 of table
Alloy 1 is prepared with full large-scale production and alloy 2-5 is prepared in pilot-scale production equipment.Melting, pouring
After casting and hot rolling, 60% cold roling reduction is subjected the material to.At different temperature and continue not on cold rolling material
Same annealing time carries out annealing test using the thermomechanical analog machines of Gleeble1500.The rate of heat addition is 200 DEG C/s and certainly
So before air cooling, 200 DEG C/s of cooldown rate drops to 400 DEG C.
Fig. 1-5 shows annealing time and annealing temperature to the alloy 1,2,3,4 and 5 respectively with different niobium (Nb) contents
Gained crystallite dimension impact.Can be observed to significantly limit grain growth by niobium alloy from accompanying drawing, because Fig. 1-5
Time-temperature coordinate system in area for example under 5 microns (μm) increase according to content of niobium is increased.Correspondingly,
Upper right is offset to corresponding to the contour line of various grain sizes, this shows to work as and adds to austenitic stainless steel of the invention
Plus the admissible scope of annealing temperature and time becomes much larger during niobium (Nb).Furthermore, it is possible to it was observed that adopt 0.11 weight %
Niobium (Nb) alloying has been realized in relatively large effect.Further increasing for niobium (Nb) content do not enter one to grain growth
The powerful effect of step.
Fig. 6 have also demonstrated the beneficial effect of niobium (Nb) content.Fig. 6 presents annealing window, i.e., limited based on experimental result
The fixed admissible combination for reaching the annealing temperature and annealing time of the crystallite dimension of 2-3 microns.It is apparent that for
For alloy 3 with 0.11 weight % niobium (Nb), the annealing window is much bigger.For example, in about 900 DEG C of temperature range, for
For alloy 1 without niobium (Nb), admissible annealing time scope is only for about 1-10s, but for 0.11 weight %
For the alloy 3 of niobium (Nb), admissible annealing time scope is 1-100s.Such difference makes the processing of alloy 3 more may be used
OK, more uniform product quality and preferable yield and efficiency are caused.
In order to study effect of the preparation in accordance with the present invention to stainless mechanical property, other two kinds of conjunctions are tested
Gold.The chemical composition of these alloys displayed in Table 2.
The chemical composition of 2 beta alloy 6 and 7 of table
Alloy 6 and 7 is prepared in pilot-scale production equipment.After fusing, casting and hot rolling, such as alloy 1-5 mono-
Sample, makes alloy 6 and 7 undergo 60% cold roling reduction.Cut from cold rolling sheet material in the angle with the 0 of rolling direction °, 45 ° and 90 °
Tensile test specimens.Tensile test specimens are annealed into 300 seconds simultaneously at a temperature of 900 DEG C and 950 DEG C in laboratory stove subsequently
And water quenching.
Table 3 present with the extension test direction of the angle of the 0 of rolling direction °, 45 ° and 90 ° on measure this
The test result of a little samples.Also show the crystallite dimension of material.Can be observed to measure in a different direction is measured
Yield strength value is closer to each other, i.e., property lies in less than high anisotropy.Survey in the horizontal and parallel direction of rolling direction
Difference between the alloy 6 of amount and 7 yield strength is less than 5%.Further, since the beneficial effect of Nb alloyings, although quite
Long annealing time, the crystallite dimension of alloy 6 and 7 are maintained at low-level,
This causes attractive mechanical property.
The result of mechanical property of the table 3 for alloy 6 and 7
Claims (9)
1. austenitic stainless steel, it is characterised in that the steel Si, 3-20% of C, 0-3% comprising 0-0.4% in terms of weight %
Nb, 0- of N, 0-0.5% of Cu, 0.05-0.5% of Mo, 0-3% of Ni, 0-3% of Cr, 0-4.5% of Mn, 10-30%
In the V of 0.5% Ti, 0-0.5%, balance of Fe and inevitable impurity, and the group of niobium (Nb), titanium (Ti) or vanadium (V)
At least one element content be more than 0.05% so that the total amount of niobium (Nb) content, titanium (Ti) content and vanadium (V) content exists
The scope of 0.05-0.5% is less than 10 microns of crystallite dimension and is rolling for having after the annealing of cold deformation product
Difference between the yield strength of the steel measured in the horizontal and parallel direction in direction processed is less than 5%.
2. austenitic stainless steel according to claim 1, it is characterised in that the crystallite dimension in the steel is less than 7 microns, and preferably
Less than 5 microns.
3. the austenitic stainless steel according to claim 1 or 2, it is characterised in that molybdenum of the ladle containing preferred 0-1.5%, and more
It is preferred that the molybdenum of 0-0.5%.
4. the austenitic stainless steel according to any one of aforementioned claim 1-3, it is characterised in that the ladle contains 0.05-0.30%
Nb, the Nb of preferred 0.05-0.20%.
5. the austenitic stainless steel according to any one of aforementioned claim 1-3, it is characterised in that the ladle contains 0.05-0.30%
Ti, the Ti of preferred 0.05-0.20%.
6. the austenitic stainless steel according to any one of aforementioned claim 1-3, it is characterised in that the ladle contains 0.05-0.30%
V, the V of preferred 0.05-0.20%.
7. be used for prepare austenitic stainless steel method, it is characterised in that before the anneal using at least 50% drafts degree
By the steel cold deformation so that 10 microns of little crystallite size is less than during annealing, the steel is in terms of weight % comprising 0-
The Cu of Mo, 0-3% of Ni, 0-3% of Cr, 0-4.5% of Mn, 10-30% of Si, 3-20% of 0.4% C, 0-3%,
The V of Ti, 0-0.5% of Nb, 0-0.5% of N, 0-0.5% of 0.05-0.5%, balance of Fe and inevitable impurity, and
And the content of at least one element in the group of niobium (Nb), titanium (Ti) or vanadium (V) is more than 0.05% so that niobium (Nb), titanium (Ti)
With the total amount of vanadium (V) 0.05-0.5% scope, and the steel measured in the horizontal and parallel direction of rolling direction
Difference between yield strength is less than 5%.
8. method according to claim 7, it is characterised in that the steel is moved back by the temperature range at 700-1050 DEG C after a deformation
Fiery 1-400 seconds, preferred 1-200 seconds.
9. the method according to claim 7 or 8, it is characterised in that this is deformed into cold rolling.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FI20145735A FI127274B (en) | 2014-08-21 | 2014-08-21 | AUSTENITIC STAINLESS STEEL WITH HIGH STABILITY AND ITS PRODUCTION METHOD |
| FI20145735 | 2014-08-21 | ||
| PCT/FI2015/050539 WO2016027009A1 (en) | 2014-08-21 | 2015-08-21 | High strength austenitic stainless steel and production method thereof |
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| CN106574351A true CN106574351A (en) | 2017-04-19 |
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| CN201580044801.0A Pending CN106574351A (en) | 2014-08-21 | 2015-08-21 | High strength austenitic stainless steel and production method thereof |
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|---|---|
| US (1) | US20170268076A1 (en) |
| EP (1) | EP3191612A4 (en) |
| JP (1) | JP2017531093A (en) |
| KR (1) | KR20170029631A (en) |
| CN (1) | CN106574351A (en) |
| FI (1) | FI127274B (en) |
| WO (1) | WO2016027009A1 (en) |
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| CN111133122A (en) * | 2017-09-25 | 2020-05-08 | 株式会社Posco | Low alloy steel sheet having excellent strength and ductility and method for manufacturing the same |
| CN112281083A (en) * | 2020-10-30 | 2021-01-29 | 上海材料研究所 | High-strength heat-resistant alloy steel having high thermal expansion characteristics and method for manufacturing same |
| CN113059153A (en) * | 2021-03-22 | 2021-07-02 | 湖南大学 | A kind of austenitic stainless steel and its laser additive preparation method |
| CN114040990A (en) * | 2019-07-17 | 2022-02-11 | 株式会社Posco | Austenitic stainless steel having improved strength and method for manufacturing the same |
| CN114934231A (en) * | 2022-05-31 | 2022-08-23 | 江西宝顺昌特种合金制造有限公司 | High-manganese low-magnetism high-strength austenitic steel and manufacturing method thereof |
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| KR101903403B1 (en) * | 2016-11-25 | 2018-10-04 | 한국기계연구원 | Austenitic stainless steel with improved pitting corrosion resistance |
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| CN111133122A (en) * | 2017-09-25 | 2020-05-08 | 株式会社Posco | Low alloy steel sheet having excellent strength and ductility and method for manufacturing the same |
| CN114040990A (en) * | 2019-07-17 | 2022-02-11 | 株式会社Posco | Austenitic stainless steel having improved strength and method for manufacturing the same |
| CN116018421A (en) * | 2020-06-23 | 2023-04-25 | 浦项股份有限公司 | High-strength austenitic stainless steel having excellent productivity and cost reduction effects and production method thereof |
| CN112281083A (en) * | 2020-10-30 | 2021-01-29 | 上海材料研究所 | High-strength heat-resistant alloy steel having high thermal expansion characteristics and method for manufacturing same |
| CN113059153A (en) * | 2021-03-22 | 2021-07-02 | 湖南大学 | A kind of austenitic stainless steel and its laser additive preparation method |
| CN114934231A (en) * | 2022-05-31 | 2022-08-23 | 江西宝顺昌特种合金制造有限公司 | High-manganese low-magnetism high-strength austenitic steel and manufacturing method thereof |
| CN115961216A (en) * | 2023-02-15 | 2023-04-14 | 山东烟炉节能科技有限公司 | Seabed oil and gas pipeline and preparation method thereof |
| CN115961216B (en) * | 2023-02-15 | 2023-08-04 | 山东烟炉节能科技有限公司 | Submarine oil and gas transmission pipeline and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| FI127274B (en) | 2018-02-28 |
| US20170268076A1 (en) | 2017-09-21 |
| KR20170029631A (en) | 2017-03-15 |
| EP3191612A4 (en) | 2018-01-24 |
| JP2017531093A (en) | 2017-10-19 |
| EP3191612A1 (en) | 2017-07-19 |
| WO2016027009A1 (en) | 2016-02-25 |
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