CN102409257B - Austenite-series heat-resistant steel and manufacturing method thereof - Google Patents
Austenite-series heat-resistant steel and manufacturing method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 68
- 239000010959 steel Substances 0.000 title claims abstract description 68
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 11
- 239000000126 substance Substances 0.000 claims abstract description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 10
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 14
- 239000000203 mixture Substances 0.000 claims description 10
- 230000032683 aging Effects 0.000 claims description 5
- 238000005242 forging Methods 0.000 claims description 4
- 239000004615 ingredient Substances 0.000 claims description 4
- 238000012545 processing Methods 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 230000006835 compression Effects 0.000 claims description 2
- 238000007906 compression Methods 0.000 claims description 2
- 238000001816 cooling Methods 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims description 2
- 238000007669 thermal treatment Methods 0.000 claims description 2
- 238000005272 metallurgy Methods 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 238000006243 chemical reaction Methods 0.000 abstract description 4
- 229910052749 magnesium Inorganic materials 0.000 abstract description 3
- 229910052735 hafnium Inorganic materials 0.000 abstract 1
- 229910052698 phosphorus Inorganic materials 0.000 abstract 1
- 239000002994 raw material Substances 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 16
- 239000000463 material Substances 0.000 description 14
- 239000013078 crystal Substances 0.000 description 12
- 239000010949 copper Substances 0.000 description 11
- 239000012071 phase Substances 0.000 description 8
- 229910052761 rare earth metal Inorganic materials 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 5
- 238000003723 Smelting Methods 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 230000033228 biological regulation Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000003628 erosive effect Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 238000003483 aging Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000000630 rising effect Effects 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 241001062472 Stokellia anisodon Species 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000002929 anti-fatigue Effects 0.000 description 1
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- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 230000002045 lasting effect Effects 0.000 description 1
- 239000000178 monomer Substances 0.000 description 1
- 229910052706 scandium Inorganic materials 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
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- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000012808 vapor phase Substances 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
The invention discloses austenite-series heat-resistant steel and a manufacturing method thereof. The austenite-series heat-resistant steel consists of the following components in percentage by mass: less than 0.03 percent of C, 0.1-2 percent of Si, 0.1-3 percent of Mn, less than 0.03 percent of P, less than 0.01 percent of S, 18-25 percent of Ni, 20-28 percent of Cr, 0.002-0.2 percent of Ti, 0.1-0.4 percent of N, 0.1-1 percent of Nb, 0.02-1 percent of V, 0.0005-0.05 percent of B, 0.1-3 percent of Cu, 0.001-0.05 percent of Sol.Al, 0.1-5 percent of optional at least one of Mo, W and Co, optional at least one of 0.0005-0.01 percent of optional Mg, 0.0005-0.2 percent of Zr, 0.0005-0.05 percent of Ca, 0.0005-0.2 percent of REM and 0.0005-0.2 percent of Hf, and the balance of iron and impurities. The austenite-series heat-resistant steel can be taken as raw materials such as steel pipes, steel plates, bar steel, forged pieces and the like used in overheaters and regenerators of boilers, chemical industrial reaction furnace pipes and the like. Moreover, the austenite-series heat-resistant steel can contain a specific amount of more than one of Mo, W and Co and/or a specific amount of more than one of Mg, Ti, Zr, Ca, REM and Hf.
Description
Technical field
The present invention relates to a kind of austenitic steel, particularly relate to a kind of austenite-series heat-resistant steel and manufacture method thereof with good hot strength and creep rupture ductility.Austenite-series heat-resistant steel of the present invention is suitable for superheater tube, reheater tube and the chemical industry of boiler with the starting material of the steel pipe of the uses such as reaction boiler tube, the steel plate that uses as the heat-resistant pressure-resistant parts, bar steel and forged steel etc.
Background technology
The quantity discharged of saving the energy and reducing carbon dioxide for protection of the environment has become the problem that the human needs faces jointly.In order to realize high efficiency, improving vapor temperature and pressure is the development trend of station boiler.The vapor temperature of present ultra-supercritical boiler is about 600 ℃, and plan will reach more than 650 ℃ gradually, even further will reach more than 700 ℃.
The High Temperature High Pressure of steam can make superheater tube, reheater tube and the chemical industry reaction boiler tube of boiler, and rises to more than 700 ℃ as the temperature in actually operating such as steel plate, bar steel and forged steel of heat-resistant pressure-resistant parts.Therefore for the steel that uses under the severe environment like this, not only require it to have good hot strength and anti-corrosion property at high temperature, and require it through still having good metal structure stability, creep rupture ductility and anti-creep fatigue feature after long-time.
Austenitic heat-resistance steel is compared with jessop has good hot strength and anti-corrosion property at high temperature.Therefore consider from intensity and erosion resistance aspect, can in can not using the high temperature range more than 650 ℃ of jessop, use austenitic heat-resistance steel.
So far, have suitable scholar and research institution to carry out a large amount of can improving simultaneously the experiment of hot strength and anti-corrosion property at high temperature, and proposed the austenite-series heat-resistant steel of a large amount of different chemical compositions, the contrast composition sees Table 1.
Representative for example SUS347H and S30432 are the 18Cr-8Ni steel of representative, and the 25Cr-20Ni take S31042, NF709 as representative is steel.Add an amount of Nb and N, improve the high temperature creep strength of material by the Nb precipitated phase of diffusion-precipitation in the high temperature creep process.
In CN 1519388A, the Ti that adds denier by combination and an amount of O and suitableization of metal structure, thus obtain a kind of creep strength height, the austenitic heat-resistance steel that the creep rupture relative reduction in area is high.
In US 6918968B2 patent, by adding an amount of Cu element, obtain rich copper precipitated phase, limit simultaneously P content, Al content and O content, thereby improve creep strength.
At above-mentioned patent and CN1340109, US 7731895B2, all guarantee as tensile strength and the high temperature creep strength of high temperature with austenite stainless steel by adding an amount of C bar none in the disclosed steel of patent documentation such as US 6939415B2, therefore the content of now general austenitic heat-resistance steel C element is all more than 0.03%, but the interpolation of C element is so that welding property decline, what is more important, in high-temperature and durable military service process, because a large amount of carbide are separated out along crystal boundary, cause high temperature creep fracture ductility and high-temperature aging impelling strength greatly to reduce.Be reduced to rapidly below the 20J more than the 200J of the normal temperature impelling strength of material before by timeliness behind 700 ℃ of 200 hours high-temperature agings, find by research, this mainly is owing to separated out a large amount of carbide along crystal boundary, thereby has reduced the impelling strength of material.
Summary of the invention
On the basis of using for reference above-mentioned practical situation, relatively existing steel grade, by restriction C content, reduce carbide separating out and enrichment at crystal boundary in the high temperature creep process, thereby improve its creep rupture ductility, by adding an amount of Cu element and boron, in the high temperature creep process, separate out copper-rich phase and boron precipitated phase simultaneously, thereby remedy the loss of the high temperature creep strength that low-carbon (LC) causes, obtain all austenitic heat-resistance steels preferably of a kind of high temperature creep strength and high temperature creep fracture ductility.
The object of the present invention is to provide a kind of 700 ℃ of temperature, under the condition of load stress 110MPa, has good creep rupture strength at high temperatures and high temperature creep fracture ductility, simultaneously at 700 ℃ of a kind of austenitic heat-resistance steels that had good impelling strength after the timeliness in lower 5000 hours.
To achieve these goals, austenite-series heat-resistant steel of the present invention, its chemical ingredients (mass percent) is: below the C:0.03, Si:0.1-2%, Mn:0.1-3% is below the P:0.03%, below the S:0.01%, Ni:18-25%, Cr:20-28%, Ti:0.002-0.2%, N:0.1-0.4%, Nb:0.1-1%, V:0.02-1%, B:0.0005-0.05%, Cu:0.1-3%, Sol.Al:0.001-0.05%, all the other are iron and impurity.
According to preferred version of the present invention, austenite-series heat-resistant steel, its chemical ingredients (mass percent) is: below the C:0.03%, Si:0.1-2%, Mn:0.1-3% is below the P:0.03%, below the S:0.01%, Ni:18-25%, Cr:20-28%, Ti:0.002-0.2%, N:0.1-0.4%, Nb:0.1-1%, V:0.02-1%, B:0.0005-0.05%, Cu:0.1-3%, Sol.Al:0.001-0.05%, and contain one or more compositions of selecting from Mo, W and Co, separately or add up to 0.1-5%; And/or contain Mg:0.0005-0.01%, Zr:0.0005-0.2%, Ca:0.0005-0.05%, REM:0.0005-0.2%, one or more compositions among the Hf:0.0005-0.2%.All the other are iron and impurity.
Below, the control reason of chemical ingredients of the present invention is described:
Below the C:0.03%
C is one of most important element of the present invention.Because carbon is the important element that consists of carbon compound.In order to ensure suitable tensile strength and the creep rupture strength at high temperatures of using austenite-series heat-resistant steel as high temperature.But the interpolation of C element is so that welding property descends, and what is more important in high-temperature and durable military service process, because a large amount of carbide is separated out along crystal boundary, causes high temperature creep fracture ductility and high-temperature aging impelling strength greatly to reduce.Be reduced to rapidly below the 20J more than the 200J of the normal temperature impelling strength of material before by timeliness behind 700 ℃ of 200 hours high-temperature agings, find by research, this mainly is owing to separated out a large amount of carbide along crystal boundary, and too much carbide presents sheet and distribute, thereby has reduced the impelling strength of material.C content is less than 0.03% the time, and the carbide of intercrystalline precipitation reduces in a large number in 700 ℃ of creep processes, so the C content of prescribed material is preferably 0.01-0.02% less than 0.03%.
Si：0.1-2％
Si adds as deoxidant element.Add in addition Si and can improve water-fast vapor-phase oxidation.In order to obtain these effects content more than 0.2% must be arranged.On the other hand, when content surpasses 2%, its processibility will be destroyed, and can worsen material structure stability at high temperature.Therefore stipulate that Si content at 0.2-2%, is preferably 0.15-0.7%.
Mn：0.1-3％
Mn and S form sulfide (MnS), improve hot workability.But its content is less than 0.1% the time and can not get above-mentioned effect.On the other hand, excessive Mn can make hardness uprise and make the steel embrittlement, destroys its processed-type and weldability.When Mn content surpassed 3%, its processibility, weldability will significantly descend.Therefore the content of stipulating Mn is preferably 0.20-3% at 0.1-3%.
Below the P:0.03%
P will sneak into inevitably as impurity, and excessive P can damage weldability and processibility significantly, so the higher limit of its content is defined as 0.03%.Preferred P content is below 0.02%, and is more few better.
Below the S:0.01%
S can sneak into inevitably as impurity, and excessive S can damage weldability and processibility, so the higher limit of its content is defined as 0.01%.Preferred S content is below 0.006%.
Ni：18-25％
Ni is the element of stable austenite tissue, also is the important element of guaranteeing erosion resistance, and its content must surpass 18%.On the other hand, when Ni 25% not only makes when above cost rise, and creep strength is descended.Therefore the content with Ni is set as 18-25%.Preferred Ni content is 19-23%.
Cr：20-28％
Cr guarantees the material scale resistance, the important element of water-fast steam oxidation, so its content must surpass 20%.On the other hand, excessive Cr can make the stability decreases of tissue, generates easily the intermetallic compound that σ equates, creep strength is descended.The increase of Cr will cause the increase be used to the high price Ni that makes the austenite structure stabilization in addition, thus so that cost rising.Especially, when the content of Cr 28% when above, the rising highly significant of the decline of creep strength and cost.Therefore, the content of regulation Cr is greater than 20% and less than 28%.Preferred Cr content is 24-28%.
Ti：0.002-0.2％
Ti can form not solid solution carbonitride, have the precipitation strength effect, therefore generally all add energetically the Ti element, in order to reach above-mentioned effect, the content of Ti element should be greater than 0.002%.But the Ti carbonitride of solid solution will not become crystal grain and form the reason that mixed crystal or inhomogeneous creep strain and ductility descend.Therefore the Ti element on be limited to 0.2%.The content of preferred Ti element is 0.004-0.012%.
Nb：0.1-1％
Nb can form minutely disperse educt of carbonitride, thereby helps to improve austenitic creep strength.Therefore, must be at least 0.1% for its content.But can damage weldability in the time of the excessive interpolation of Nb, especially weldability can significantly descend when its content surpasses 1%.Therefore, the content of regulation Nb is at 0.1-1%.In addition, Nb content is preferably 0.3-0.9%.
V：0.01-1％
V can form the carbonitride disperse educt, thereby improves the creep strength of material.But its content can not get above-mentioned effect less than 0.01% the time.On the other hand, when surpassing 1%, content can produce the embrittlement phase.Therefore the content of V is set in 0.01-1%.In addition, be preferably 0.03-0.2% as V content, more preferably 0.09-0.9%.
B：0.0005-0.05％
B replaces a carbon part that forms carbonitride, is present in the carbonitride, perhaps is present in the crystal boundary as the B monomer, has the effect of the intercrystalline slip creep that produces under the high temperature that is suppressed at more than 700 ℃.But its content can not get this effect when following 0.0005%.On the other hand, when surpassing 0.2%, content can damage weldability.Therefore the content with B is set as below the 0.0005-0.05%, is preferably 0.002-0.02%.
Sol.Al：0.0005-0.03％
Al adds as deoxidant element.In order to obtain deoxidation effect, the content of Sol.Al must be more than 0.0005%.On the other hand, Al is excessive to add fashionable stability that can damaging tissue, produces the embrittlement of σ phase, and particularly when in Sol.Al, σ phase embrittlement meeting was very remarkable when Al content surpassed 0.03%.Therefore the content with Al is set in 0.0005-0.03%, is preferably 0.007-0.035%.
N：0.1-0.4％
N adds for the Ni precipitation hardened and replacement part high price that is caused by carbonitride guarantees the high-temperature stability of austenite structure.In order to improve tensile strength and high temperature creep strength, N content must be more than 0.1%, but the excessive interpolation of N can damage its ductility, weldability and toughness, and especially when its content surpassed 0.4%, ductility, weldability and toughness descended very remarkable.Therefore the content with N is set in 0.1-0.4%, is preferably 0.16-0.35%.
Cu：0.1-3％
Cu is for the rich copper precipitated phase of formation in the high temperature creep process, thereby improves the high temperature creep strength of material.In order to reach above-mentioned effect, must be at least 0.1% for its content.But can damage its processibility in the time of the excessive interpolation of Cu, especially its hot workability can significantly descend when its content surpasses 3%.Therefore, the content of regulation Cu is preferably 0.3-2.4% at 0.1-3%.
Austenitic heat-resistance steel of the present invention, except containing above-mentioned composition, rest part is in fact Fe, in other words conj.or perhaps by Fe and above-mentioned beyond impurity formed.
In the above-mentioned austenite-series heat-resistant steel of the present invention another is the steel of at least a composition selected in any one group or two groups that contains from following first group and second group.The below describes their composition.
First group (Co, Mo and W)
Co, Mo and W are the effective elements that improves high temperature creep strength.Therefore preferably actively add among Co, Mo and the W more than one in order to obtain this effect, separately or add up to add-on can obtain this effect 0.1% when above.On the other hand, the excessive interpolation of Co, Mo and W can damage toughness, intensity and ductility.Co, Mo and W are powerful ferrite formers in addition, and for the stability that realizes austenite structure must increase the amount of Ni thereby can make price increase, therefore higher limit independent or total content is better with 5%.Independent or the total content of Co, Mo and W is 0.5-2%.
Second group (Mg, Zr, Ca, REM and Hf)
Mg, Zr, Ca, REM and Hf, any fixedly effective element of S, raising hot workability that is.Mg also has the denier of adding and just has deoxidation effect in addition.The excessive interpolation of Zr is the reason that forms oxide compound and nitride, causes mixed crystal, can play the effect of strengthening the grain boundary but add trace.REM can form harmless and stable oxide compound, thereby has the raising erosion resistance, the effect of creep ductility, heat-resistant anti-fatigue characteristic and creep strength.
Therefore when wanting to obtain this effect, be preferably and add energetically wherein more than one, in order to obtain above-mentioned effect, the content of any element all will be more than 0.0005% in this group element.On the other hand, when surpassing 0.01%, can damage the content of Mg steel, infringement creep strength, creep fatigue characteristic and ductility.When the content of Zr surpassed 0.2%, it formed oxide compound and nitride, thereby not only can cause the reason of mixed crystal, and can damage steel, infringement creep strength, creep fatigue characteristic, further can damage its ductility.When Ca content surpasses 0.05%, can damage ductility and processing characteristics, and bring sizable difficulty to smelting.When the content of REM and Hf surpasses 0.2%, because oxide compound foreign material of equal value are more, not only can damage weldability but also can cause cost to rise.
Therefore, the content of each element during interpolation, preferably Mg is 0.0005-0.01%, and any among Zr, REM and the Hf is 0.0005-0.2%, and Ca is 0.0005-0.05%.
Preferably, any among Mg and the Ca is 0.002-0.01%.Any among REM, Zr and the Hf is 0.02-0.05%.
The said REM of the present invention, i.e. rare earth element refers in 17 kinds of elements of Sc, Y and group of the lanthanides one or more.
Of the present invention have above-mentioned chemical constitution and metal structure and have good hot strength and the austenitic heat-resistance steel of creep rupture ductility, can be produced as follows.
Smelt at vacuum smelting furnace;
Be cast into steel ingot;
Carry out compression ratio greater than 3 forging or rolling processing;
Because the Nb element needs for a long time fully solid solution of ability of high temperature.But the long-time solution treatment meeting of high temperature so that crystal grain too grow up.
In order both to allow the abundant solid solution of Nb element, do not allow again crystal grain too grow up, before final cold or hot-work, steel need to be heated at least one times (preferable range is 1200-1230 ℃) more than 1200 ℃, water-cooled is to the intermediate heat treatment of room temperature after soaking time 20-90 minute.
After final cold or hot-work, be heated to more than 1230 ℃ (preferable range is 1230-1260 ℃) and carry out final thermal treatment, soaking time is 5-30 minute, water-cooled is to room temperature.
Embodiment
Below by embodiment the present invention is more specifically illustrated, but the present invention is not restricted to the following example.
Smelting has 19 kinds of steel of chemical constitution shown in the table 1.Wherein No.1-12 kind steel is embodiment, and No.13-19 kind steel is Comparative Examples.
For the steel of No.1-19, utilizing capacity is that 50 kilograms vacuum smelting furnace is smelted, and the steel ingot that casting is obtained utilizes following method to make sheet material.
Manufacture method
The first operation: be heated to 1200 ℃.
The second operation: be more than 3 by forging ratio, final forging temperature is configured as the steel plate that thickness is 60mm greater than 1050 ℃ heat forged.
The 3rd operation: air cooling is to room temperature.
The 4th operation: be heated to 1200 ℃, then be rolled into the sheet material of thickness 15mm, water-cooled is to room temperature subsequently.
The 5th operation: be heated to 1230 ℃, be incubated after 15 minutes water-cooled to room temperature.
The sheet material that obtains is got cylindric lasting sample, and 700 ℃ of temperature, load stress is to carry out the high temperature creep test under the condition of 110MPa, obtains its rupture time (h) and fracture relative reduction in area (%).And the impelling strength of 700 ℃ of timeliness after 1000 hours is carried out in selection.It the results are shown in Table 2.
The performance of table 2 embodiment of the invention and Comparative Examples
As seen from Table 2, austenitic heat-resistance steel of the present invention has good hot strength and creep rupture ductility.This steel is suitable for superheater tube, reheater tube and the chemical industry of boiler with the starting material of the steel pipe of the uses such as reaction boiler tube, the steel plate that uses as the heat-resistant pressure-resistant parts, bar steel and forged steel etc.
Claims (9)
1. austenite-series heat-resistant steel, the mass percent of its chemical ingredients is: below the C:0.03, Si:0.1-2%, Mn:0.1-3% is below the P:0.03%, below the S:0.01%, Ni:18-25%, Cr:20-28%, Ti:0.002-0.2%, N:0.1-0.4%, Nb:0.1-1%, V:0.02-1%, B:0.0005-0.05%, Cu:0.1-3%, Sol.Al:0.001-0.05%, optional Mo, W and at least a composition among the Co, content is 0.1-5%; Optional Mg:0.0005-0.01%, Zr:0.0005-0.2%, Ca:0.0005-0.05%, REM:0.0005-0.2%, at least a composition among the Hf:0.0005-0.2%, all the other are iron and inevitable impurity.
2. austenite-series heat-resistant steel as claimed in claim 1 is characterized in that, C:0.01-0.02%, Si:0.15-0.7%, Mn:0.20-3% is below the P:0.02%, below the S:0.006%, Ti:0.004-0.012%, N:0.16-0.35%, Nb:0.3-0.9%, V:0.09-0.9%, B:0.002-0.02%, Cu:0.3-2.4%, Sol.Al:0.007-0.035%.
3. austenite-series heat-resistant steel as claimed in claim 1 or 2 is characterized in that, Ni:19-23%, Cr:24-28%.
4. austenite-series heat-resistant steel as claimed in claim 1 or 2 is characterized in that, the optional at least a composition that is selected among Mo, W and the Co that contains, separately or add up to 0.5-2%.
5. austenite-series heat-resistant steel as claimed in claim 1 or 2 is characterized in that, any among Mg and the Ca is 0.002-0.01%.
6. austenite-series heat-resistant steel as claimed in claim 1 or 2 is characterized in that, any among REM, Zr and the HF is 0.02-0.05%.
7. such as the manufacture method of the arbitrary described austenite-series heat-resistant steel of claim 1-6, comprise: after metallurgy and foundry, carry out compression ratio greater than 3 forging or rolling processing, before final cold or hot-work, water-cooled was to the intermediate heat treatment of room temperature after steel was heated to more than 1200 ℃ at least one times; After final cold or hot-work, steel is heated to carries out final thermal treatment more than 1230 ℃, soaking time is 5-30 minute, with the water-cooling pattern cool to room temperature.
8. the manufacture method of austenite-series heat-resistant steel as claimed in claim 7 is characterized in that, before final cold or hot-work, steel is heated to 1200-1230 ℃ at least one times; After final cold or hot-work, steel is heated to 1230-1260 ℃.
9. the creep fracture time under the austenite-series heat-resistant steel of making such as claim 7 or 8 described methods, its 700 ℃, 110MPa is more than 9600h; Its creep rupture relative reduction in area under 700 ℃, 110MPa is more than 20%; Room-temperature aging impelling strength Akv at 700 ℃, 5000 hours is more than the 20J.
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| CN102676951A (en) * | 2012-05-08 | 2012-09-19 | 宝山钢铁股份有限公司 | Austenitic heat-resistant steel and manufacturing method thereof |
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| CN107475640B (en) * | 2017-08-08 | 2018-05-22 | 永兴特种不锈钢股份有限公司 | A kind of preparation method of the austenitic heat-resistance steel of the anti-steam corrosion of high-lasting strength |
| CN107299292B (en) * | 2017-08-08 | 2018-09-11 | 永兴特种不锈钢股份有限公司 | A kind of austenitic heat-resistance steel of the anti-steam corrosion of high-lasting strength |
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| JP7372537B2 (en) * | 2019-12-27 | 2023-11-01 | 日本製鉄株式会社 | Austenitic heat-resistant steel |
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| CN113832412B (en) * | 2021-09-09 | 2023-12-05 | 中车戚墅堰机车车辆工艺研究所有限公司 | Heat treatment method of Nb-containing Cr-Ni cast austenitic heat-resistant stainless steel |
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| CN115011879B (en) * | 2022-06-23 | 2024-02-06 | 西北工业大学 | Austenitic heat-resistant steel and heat treatment method thereof |
| CN115896442A (en) * | 2022-11-08 | 2023-04-04 | 内蒙古中天宏远稀土新材料股份公司 | Bottom roll for gadolinium steel heating furnace, preparation method thereof and application of tungsten element |
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