CN106636842A - Precipitation-strengthened high-carbon austenitic heat-resistant steel and preparation method thereof - Google Patents
Precipitation-strengthened high-carbon austenitic heat-resistant steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 55
- 239000010959 steel Substances 0.000 title claims abstract description 55
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 24
- 238000002360 preparation method Methods 0.000 title claims description 18
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 42
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 40
- 238000001556 precipitation Methods 0.000 claims abstract description 24
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 19
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 18
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 28
- 229910052710 silicon Inorganic materials 0.000 claims description 28
- 230000008018 melting Effects 0.000 claims description 12
- 238000002844 melting Methods 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 12
- 238000009749 continuous casting Methods 0.000 claims description 8
- 230000006698 induction Effects 0.000 claims description 8
- 239000006185 dispersion Substances 0.000 claims description 4
- 210000001161 mammalian embryo Anatomy 0.000 claims description 4
- 230000003647 oxidation Effects 0.000 claims description 3
- 238000007254 oxidation reaction Methods 0.000 claims description 3
- 239000002244 precipitate Substances 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 2
- 239000011159 matrix material Substances 0.000 claims description 2
- 239000000470 constituent Substances 0.000 claims 1
- 239000002245 particle Substances 0.000 claims 1
- 239000000956 alloy Substances 0.000 abstract description 66
- 229910045601 alloy Inorganic materials 0.000 abstract description 64
- 230000000694 effects Effects 0.000 abstract description 9
- 230000005496 eutectics Effects 0.000 abstract description 2
- 239000010955 niobium Substances 0.000 abstract 6
- 239000010936 titanium Substances 0.000 abstract 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract 1
- 238000005728 strengthening Methods 0.000 abstract 1
- 239000011651 chromium Substances 0.000 description 29
- 239000011572 manganese Substances 0.000 description 26
- 239000012452 mother liquor Substances 0.000 description 16
- 239000000243 solution Substances 0.000 description 10
- 239000013078 crystal Substances 0.000 description 8
- 238000010792 warming Methods 0.000 description 8
- 239000000463 material Substances 0.000 description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- 241001062472 Stokellia anisodon Species 0.000 description 6
- 239000012535 impurity Substances 0.000 description 6
- 239000002994 raw material Substances 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 4
- 230000002411 adverse Effects 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 238000007788 roughening Methods 0.000 description 3
- VGGSQFUCUMXWEO-UHFFFAOYSA-N Ethene Chemical compound C=C VGGSQFUCUMXWEO-UHFFFAOYSA-N 0.000 description 2
- 239000005977 Ethylene Substances 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 239000003245 coal Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000003365 glass fiber Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000010248 power generation Methods 0.000 description 2
- 150000002910 rare earth metals Chemical group 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 101001055216 Homo sapiens Interleukin-9 Proteins 0.000 description 1
- 102100026871 Interleukin-9 Human genes 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- -1 Rare Earth Carbides Chemical class 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000006399 behavior Effects 0.000 description 1
- 150000001722 carbon compounds Chemical class 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000005516 engineering process Methods 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
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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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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- 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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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Treatment Of Steel In Its Molten State (AREA)
Abstract
The novel precipitation strengthening high-carbon austenitic heat-resistant steel has the alloy components meeting the following range requirements in percentage by mass: c: 0.5-0.8%, Cr: 24-28%, Ni: 35-50%, Co: less than or equal to 3.0 percent, Mn: less than or equal to 2.0 percent, Si: 1.5-3.0%, Nb: less than or equal to 1.0%, W: less than or equal to 7.5 percent, Ti: 0.5-2.5% and the balance Fe. Wherein the content of Ti and Nb satisfies that Ti/Nb is more than or equal to 0.7; ti + Nb is more than or equal to 2. The alloy prepared by the process eliminates coarse eutectic carbide in the as-cast alloy structure on the premise of ensuring higher carbide volume fraction, and inhibits Cr (niobium) and titanium) because a large amount of (Nb, Ti) C is uniformly dispersed and distributed in the alloy23C6Coarsening and growing up, and playing a good effect on the stability of alloy structure and performance.
Description
Technical field
The invention belongs to material and field of material preparation, be related to it is a kind of with high-volume fractional and size small stable carbon
A kind of compound precipitation strength Novel austenitic heat-resistance steel, and in particular to precipitation strength high-carbon austenitic heat-resistance steel, is particularly well-suited to
In the part of Long-Time Service under worst hot case, the such as cracking furnace pipe in ethylene production and HK-40 Tube at Hydrogen Reformer, thermal power generation unit
The parts such as the sedimentator in coal burner nozzle and boiler reheater, glass fiber industry.
Background technology
Under worst hot case during long service, the carbide of higher volume fraction is that alloy obtains good elevated temperature strength to alloy
Important leverage.The heat resisting steel for using at high temperature at present generally has higher Cr, C content, by being formed greatly in grain boundaries
The nascent Cr of size23C6And grain boundaries separate out the secondary Cr of small and dispersed distribution23C6And make alloy obtain excellent elevated temperature strength
Performance.However, alloy is under high temperature or low temperature condition of high ground stress during long service, Cr23C6Grow up tendency with higher roughening,
And then cause alloy property to decline rapidly with the prolongation of use time.Additionally, grain boundaries form the Cr of large-size23C6Meeting
Cause its interface Cr elements barren, and then cause alloy sensitization phenomenon occur, material corrosion resistance is adversely affected.
To make alloy obtain more stable microstructure and property at high temperature, in recent years people have carried out a series of trials, as a result confirm
The addition of Nb elements can be formed and the alternatively distributed NbC of chromium carbide in crystal boundary.Because the latter is sufficiently stable at high temperature, taking
Its change in size is little during labour, while inhibiting Cr to a great extent23C6Roughening grow up.Wherein, it is most representative
Be to add a small amount of Nb elements in HP40 alloy cast tubes, obtain the HP40Nb with higher structure stability and rupture ductility
Alloy, so that material obtains longer service life.
Even so, carbide size is still larger in the high C content austenitic steel for using at present.These carbide are solidifying
Gu during directly formed by liquid phase, it is impossible to eliminated by solution treatment.These thick primary carbides often band
Come many other problems, such as alloy its obstruction dislocation movement in deformation process, and then cause dislocation pile up and cause stress
Concentrate, it is final to promote crack initiation and along carbide extension；Meanwhile, the carbide of alloy large-size under thermal stress effect
Larger adverse effect can be caused to the thermal fatigue property of alloy；Additionally, the carbide of large-size also can be to the processing of alloy
Performance is brought more highly difficult.Therefore, on the basis of carbide volume fraction is ensured, alloy structure is further improved especially thin
Change carbide size, the processing and performance to material has material impact.
Adding alterant in alloy molten steel can be such that As-cast Microstructure is significantly refined, but the addition of alterant has
Serious harm may be caused to the mechanical property of material in the form of being mingled with alloy.The addition of rare earth element can be with
Rare Earth Carbides are formed from liquid phase, and then promotes carbide size refinement as equiax crystal.However, adding rare earth unit on a small quantity
Element is limited to the effect of alloy structure refinement, and excessively adds rare earth then can bring adverse effect to alloy property.
The content of the invention
To overcome the problems of the prior art, it is an object of the invention to provide a kind of precipitation strength high-carbon austenite heat-resistance
Steel, by adjusting Ti, Nb weight/mass percentage composition, it is ensured that TiC plays fully refinement carbonization as equiax crystal during alloy graining
The effect of thing；Simultaneously, it is ensured that the MC type carbide containing enough volume fractions in alloy, so as to obtain stable alloy structure
The purpose of energy.
In order to realize above goal of the invention, the technical solution adopted in the present invention is：
A kind of precipitation strength high-carbon austenitic heat-resistance steel, by mass percentage, each element content in the heat-resisting composition of steel
Meet：C：0.5～0.8%, Cr：24～28%, Ni：35～50%, Co：≤ 3.0%, Mn：≤ 2.0%, Si：1.5～
3.0%, Nb：≤ 1.5%, W：≤ 7.5%, Ti：0.5～2.5%, balance of Fe；Wherein, Ti, Nb mass percentage content expires
Sufficient Ti/Nb >=0.7；Meanwhile, Ti+Nb >=2.
The present invention is further improved by, and by mass percentage, each element content meets in the heat-resisting composition of steel：C：
0.5～0.8%, Cr：24～28%, Ni：35～50%, Co：≤ 3.0%, Mn：≤ 2.0%, Si：1.5～3.0%, Nb：≤
1.5%, W：5≤7.5%, Ti：0.5～2.5%, balance of Fe；Wherein, Ti, Nb mass percentage content meet Ti/Nb >=
0.7；Meanwhile, Ti+Nb >=2.
The present invention is further improved by, the as-cast structure of the heat resisting steel by austenitic matrix and (Nb, Ti) C with
Cr23C6Two kinds of carbide are constituted；And carbide volume fraction is not less than 12%, and (Nb, Ti) C accounts for carbide percent by volume
It is not less than 30%.
The present invention is further improved by, and (Nb, Ti) the C even dispersions are distributed in intra-die, its average-size
Less than 5 microns；Ti is present in (Nb, Ti) C granular centers position as equiax crystal, and its average-size to be not more than 1 micro-
Rice；Cr23C6；In herring-bone form Dispersed precipitate in transgranular, its average-size is less than 10 microns.
The present invention is further improved by, and the hardness of the heat resisting steel is not less than 240HV, in 1000 DEG C and 1100 DEG C surrenders
Intensity is respectively higher than 60MPa and 35MPa, and at 1050 DEG C, oxidation rate is less than 1.8 × 10-11g2cm-4s-1。
The present invention is further improved by, and when heat resisting steel service temperature is higher than 900 DEG C, is first being carried out using front
1080-1120 DEG C/3-5h solution treatment.
A kind of preparation method of precipitation strength high-carbon austenitic heat-resistance steel, when being prepared using induction furnace melting, molten steel cast
Temperature control is in the range of 1560-1630 DEG C.
The present invention is further improved by, and when being prepared using continuous casting process after melting, continuous casting draws embryo speed to be less than 1.2m/
min。
Compared to the prior art the present invention is had advantageous effect in that：The present invention on the basis of HP40Nb alloys,
Ni, Cr, C, W are to promote alloy to obtain more preferable high-temperature behavior and structure stability in adjustment alloy, while the higher Ti of addition
Element simultaneously screens rational Ti/Nb, and Ti, Nb weight/mass percentage composition meets Ti/Nb >=0.7, using guarantee during alloy graining TiC as
Equiax crystal and play the effect of abundant refined carbides；Meanwhile, Ti+Nb >=2 to guarantee alloy in contain enough volume fractions
MC type carbide, so as to obtain the purpose of stable alloy structure performance.Because TiC has high fusing point steady with good
Qualitative, it can be straight by liquid phase in the form of tiny TiC (average-size is not more than 1 micron) after Ti contents reach to a certain degree
Connect precipitation and promote carbide refinement as equiax crystal.On this basis by the nascent chromium carbide body of the present bulk of solution treatment
Fraction is final to obtain the New Heat-Resistant Steel with good organization's stability and elevated temperature strength performance in relatively low scope.This
Invention has further the advantage that：
1. heat resisting steel of the present invention possesses higher carbide volume fraction, while carbide size is tiny and disperse divides
It is distributed in intra-die.
2. heat resisting steel of the present invention has during one's term of military service good structure stability, and carbide growth speed is slow.
3. the alloy for preparing by the method for the invention eliminates casting on the premise of higher carbon compound volume fraction is ensured
Thick eutectic carbide in state alloy structure, and due to a large amount of (Nb, Ti) C of even dispersion distribution in alloy, it is suppressed that Cr23C6
Roughening is grown up, and to alloy structure and stability good effect is served, and possesses good combination property and tissue stabilization
Property, its hardness is not less than 240HV, in 1000 DEG C and 1100 DEG C of yield strengths 60MPa and 35MPa is respectively higher than, at 1050 DEG C
Oxidation rate is less than 1.8 × 10-11g2cm-4s-1.Alloy of the present invention is applied to the part of Long-Time Service under worst hot case, such as
Cracking furnace pipe in ethylene production and coal burner nozzle in HK-40 Tube at Hydrogen Reformer, thermal power generation unit and boiler reheater,
The parts such as the sedimentator in glass fiber industry.
Further, a large amount of discontinuous (Nb, Ti) C of intercrystalline precipitation after solution treatment, and transgranular (Nb, Ti) C sizes change
Become not substantially, while transgranular Cr23C6A large amount of dissolvings, it accounts for carbide proportion and is not higher than 20%.
Description of the drawings
Fig. 1 is the alloy Analysis on Microstructure of embodiment 1.
Fig. 2 is that TiC is present in NbC core positions as equiax crystal in the 2-in-1 gold of embodiment.
Fig. 3 is morphology of carbides after the process of the alloy solid solution of embodiment 3.
Specific embodiment
The present invention is described in further detail with reference to embodiment.
Embodiment 1
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, by mass percentage, including：C：0.7%, Cr：
25%, Ni：45%, Mn：1.0%, Si：2.5%, Nb：1.0%, W：5.0%, Ti：1.0%, balance of Fe.In this embodiment,
Ti, Nb mass percentage content meets Ti/Nb >=0.7, and Ti+Nb >=2.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.7%, Cr：25%, Ni：45%, Mn：1.0%, Si：
2.5%, Nb：1.0%, W：5.0%, Ti：1.0%, balance of Fe, by above-mentioned mass percent alloyage；
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, molten steel adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls the quality of P, S impurity element in mother liquor
The equal ＜ 0.03% of degree, cast of subsequently coming out of the stove after molten steel temperature reaches 1580 DEG C.
Embodiment 2
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, by mass percentage, including：C：0.75%, Cr：
28%, Ni：48%, Mn：1.5%, Si：2.1%, Nb：0.5%, W：7.5%, Ti：1.6%, balance of Fe.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.75%, Cr：28%, Ni：48%, Mn：1.5%, Si：
2.1%, Nb：0.5%, W：7.5%, Ti：1.6%, balance of Fe., by above-mentioned mass percent alloyage；
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, molten steel adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls the quality of P, S impurity element in mother liquor
The equal ＜ 0.03% of degree, cast of subsequently coming out of the stove after molten steel temperature reaches 1600 DEG C.
Embodiment 3
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, includes by mass percentage：C：0.75%, Cr：27%,
Ni：49%, Mn：1.2%, Si：2.4%, Nb：1.2%, W：7.0%, Ti：0.9%, balance of Fe.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.75%, Cr：27%, Ni：49%, Mn：1.2%, Si：
2.4%, Nb：1.2%, W：7.0%, Ti：0.9%, balance of Fe, by above-mentioned mass percent alloyage；
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, alloy mother liquor adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls P, S impurity element in mother liquor
The equal ＜ 0.03% of mass percentage content, cast of subsequently coming out of the stove after molten steel temperature reaches 1600 DEG C.
3) solution treatment：By step 2) come out of the stove cast after alloy pig be put into heat-treatment furnace, with the speed of 50 DEG C/min
After being warming up to 1000 DEG C, 1100 DEG C are warming up to the speed of 10 DEG C/min, and after being incubated 5 hours at 1100 DEG C, are air cooled to room temperature.
Referring to table 1, the alloy material mechanical property of embodiment 1-3 is tested respectively, it is seen that alloy is in 1000-
Possess excellent elevated temperature strength performance, beta alloy compression yield strength point in 1000 DEG C and 1100 DEG C in the range of 1100 DEG C
Not Gao Yu 60MPa and 35MPa, alloy rigidity is not less than 240HV.
Referring to Fig. 1, the microstructure of alloy described in embodiment 1 is observed, As-cast Microstructure is by austenite base
Body and (Nb, Ti) C and Cr23C6Two kinds of carbide are constituted.(Nb, Ti) C even dispersions are distributed in intra-die, Cr23C6Size
It is relatively large, in herring-bone form Dispersed precipitate in transgranular.
Referring to Fig. 2, alloy microstructure described in embodiment 2 is observed, visible size is tiny at crystal boundary NbC cores
TiC, and its size is not less than 1 micron.
Referring to Fig. 3, alloy microstructure described in embodiment 3 is observed, intercrystalline precipitation is a large amount of not after solution treatment
Continuous (Nb, Ti) C, and transgranular (Nb, Ti) C sizes change substantially, while transgranular Cr23C6A large amount of dissolvings, it accounts for carbide ratio
Example not higher than 20%.
The embodiment alloy mechanical property test result of table 1
When being prepared using continuous casting process after heat resisting steel melting of the present invention, continuous casting draws embryo speed to be less than 1.2m/min.
Embodiment 4
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, includes by mass percentage：C：0.5%, Cr：24%,
Ni：35%, Co：1.0%, Mn：0.1%, Si：3%, Nb：0.2%, W：1.0%, Ti：2%, balance of Fe.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.5%, Cr：24%, Ni：35%, Co：1.0%, Mn：
0.1%, Si：3%, Nb：0.2%, W：1.0%, Ti：2%, balance of Fe.By above-mentioned mass percent alloyage；
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, alloy mother liquor adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls P, S impurity element in mother liquor
The equal ＜ 0.03% of mass percentage content, cast of subsequently coming out of the stove after molten steel temperature reaches 1560 DEG C.
3) solution treatment：By step 2) come out of the stove cast after alloy pig be put into heat-treatment furnace, with the speed of 50 DEG C/min
After being warming up to 1000 DEG C, 1080 DEG C are warming up to the speed of 10 DEG C/min, and after being incubated 5 hours at 1080 DEG C, are air cooled to room temperature.
When being prepared using continuous casting process after melting, continuous casting draws embryo speed to be less than 1.2m/min.
Embodiment 5
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, includes by mass percentage：C：0.8%, Cr：28%,
Ni：50%, Co：2.0%, Mn：1%, Si：1.5%, Nb：1%, W：0.1%, Ti：2.5%, balance of Fe.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.8%, Cr：28%, Ni：50%, Co：2.0%, Mn：
1%, Si：1.5%, Nb：1%, W：0.1%, Ti：2.5%, balance of Fe.
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, alloy mother liquor adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls P, S impurity element in mother liquor
The equal ＜ 0.03% of mass percentage content, cast of subsequently coming out of the stove after molten steel temperature reaches 1630 DEG C.
3) solution treatment：By step 2) come out of the stove cast after alloy pig be put into heat-treatment furnace, with the speed of 50 DEG C/min
After being warming up to 1000 DEG C, 1120 DEG C are warming up to the speed of 10 DEG C/min, and after being incubated 3 hours at 1120 DEG C, are air cooled to room temperature.
Embodiment 6
The precipitation strength high-carbon austenitic heat-resistance steel of the present embodiment, includes by mass percentage：C：0.6%, Cr：26%,
Ni：40%, Co：3%, Mn：2%, Si：1.8%, Nb：1.2%, W：3.0%, Ti：0.9%, balance of Fe.
The preparation method of the present embodiment heat resisting steel is comprised the following steps：
1) raw material is prepared：Composition includes by mass percentage：C：0.6%, Cr：26%, Ni：40%, Co：3%, Mn：
2%, Si：1.8%, Nb：1.2%, W：3.0%, Ti：0.9%, balance of Fe.
2) melting step：All elements in mentioned component in addition to Si and Mn are melted the alloy of preparation using induction furnace
Alloy mother liquor is smelt, alloy mother liquor adds silicon and manganese deoxidation after reaching more than 1500 DEG C, and controls P, S impurity element in mother liquor
The equal ＜ 0.03% of mass percentage content, cast of subsequently coming out of the stove after molten steel temperature reaches 1600 DEG C.
3) solution treatment：By step 2) come out of the stove cast after alloy pig be put into heat-treatment furnace, with the speed of 50 DEG C/min
After being warming up to 1000 DEG C, 1100 DEG C are warming up to the speed of 10 DEG C/min, and after being incubated 4 hours at 1100 DEG C, are air cooled to room temperature.
Claims (8)
1. a kind of precipitation strength high-carbon austenitic heat-resistance steel, it is characterised in that：By mass percentage, it is each in the heat-resisting composition of steel
Constituent content meets：C：0.5～0.8%, Cr：24～28%, Ni：35～50%, Co：≤ 3.0%, Mn：≤ 2.0%, Si：
1.5～3.0%, Nb：≤ 1.5%, W：≤ 7.5%, Ti：0.5～2.5%, balance of Fe；Wherein, Ti, Nb mass percent contains
Amount meets Ti/Nb >=0.7；Meanwhile, Ti+Nb >=2.
2. a kind of precipitation strength high-carbon austenitic heat-resistance steel according to claim 1, it is characterised in that：By weight percent
Meter, each element content meets in the heat-resisting composition of steel：C：0.5～0.8%, Cr：24～28%, Ni：35～50%, Co：≤
3.0%, Mn：≤ 2.0%, Si：1.5～3.0%, Nb：≤ 1.5%, W：5≤7.5%, Ti：0.5～2.5%, balance of Fe；
Wherein, Ti, Nb mass percentage content meets Ti/Nb >=0.7；Meanwhile, Ti+Nb >=2.
3. a kind of precipitation strength high-carbon austenitic heat-resistance steel according to claim 1, it is characterised in that：The casting of the heat resisting steel
State is organized by austenitic matrix and (Nb, Ti) C and Cr23C6Two kinds of carbide are constituted；And carbide volume fraction is not less than
12%, and (Nb, Ti) C accounts for carbide percent by volume and is not less than 30%.
4. a kind of precipitation strength high-carbon austenitic heat-resistance steel according to claim 3, it is characterised in that：(Nb, the Ti) C
Even dispersion is distributed in intra-die, and its average-size is less than 5 microns；Ti is present in (Nb, Ti) C particles as equiax crystal
Center, and its average-size is not more than 1 micron；Cr23C6；In herring-bone form Dispersed precipitate in transgranular, its average-size is little
In 10 microns.
5. a kind of precipitation strength high-carbon austenitic heat-resistance steel according to claim 1, it is characterised in that：The heat resisting steel it is hard
Degree is not less than 240HV, is respectively higher than 60MPa and 35MPa in 1000 DEG C and 1100 DEG C of yield strengths, the oxidation rate at 1050 DEG C
Less than 1.8 × 10-11g2cm-4s-1。
6. a kind of precipitation strength high-carbon austenitic heat-resistance steel according to claim 1, it is characterised in that：When heat resisting steel is on active service
When temperature is higher than 900 DEG C, using front 1080-1120 DEG C/3-5h solution treatment is first being carried out.
7. a kind of preparation method of precipitation strength high-carbon austenitic heat-resistance steel as claimed in claim 1, it is characterised in that：Using
When prepared by induction furnace melting, molten steel pouring temperature is controlled in the range of 1560-1630 DEG C.
8. the preparation method of precipitation strength high-carbon austenitic heat-resistance steel according to claim 7, it is characterised in that：After melting
When being prepared using continuous casting process, continuous casting draws embryo speed to be less than 1.2m/min.
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Citations (4)
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|---|---|---|---|---|
| JPH04280938A (en) * | 1991-03-08 | 1992-10-06 | Daido Steel Co Ltd | Production of ni-base superalloy member |
| CN1258756A (en) * | 1999-12-17 | 2000-07-05 | 黄进峰 | High-temperature high-strength antioxidant anticorrosive austenite alloy |
| CN104040012A (en) * | 2011-12-20 | 2014-09-10 | Ati资产公司 | High strength, corrosion resistant austenitic alloys |
| CN104195474A (en) * | 2014-07-30 | 2014-12-10 | 保定风帆精密铸造制品有限公司 | High-temperature-resistant alloy casting and preparation method thereof |
-
2016
- 2016-09-18 CN CN201610829408.9A patent/CN106636842A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04280938A (en) * | 1991-03-08 | 1992-10-06 | Daido Steel Co Ltd | Production of ni-base superalloy member |
| CN1258756A (en) * | 1999-12-17 | 2000-07-05 | 黄进峰 | High-temperature high-strength antioxidant anticorrosive austenite alloy |
| CN104040012A (en) * | 2011-12-20 | 2014-09-10 | Ati资产公司 | High strength, corrosion resistant austenitic alloys |
| CN104195474A (en) * | 2014-07-30 | 2014-12-10 | 保定风帆精密铸造制品有限公司 | High-temperature-resistant alloy casting and preparation method thereof |
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