CN108699661A - The austenitic steel of having excellent high-temperature strength - Google Patents
The austenitic steel of having excellent high-temperature strength Download PDFInfo
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- CN108699661A CN108699661A CN201780014102.0A CN201780014102A CN108699661A CN 108699661 A CN108699661 A CN 108699661A CN 201780014102 A CN201780014102 A CN 201780014102A CN 108699661 A CN108699661 A CN 108699661A
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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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- 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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Present document relates to while the expensive alloying element Ni for including largely in substituting the high temperature resistant stainless steel that such as turbocharger uses at extreme temperatures with the alloying element of low cost, additionally it is possible to realize the high temperature physical property for being equal to or higher than traditional heat-resistance stainless steel.The austenitic steel of the present invention, which is characterized in that include C:0.4 to 0.5 weight %, Si:1.0 to 2.0 weight %, Mn:5.0 to 8.0 weight %, Ni:13.5 to 16.5 weight %, Cr:23 to 26 weight %, remaining is the ratio of Mn contents and Ni contents in Fe and other inevitable impurity and the alloying element, CMn/CNiIt is maintained in the range of 0.3 to 0.9.
Description
Technical field
The present invention relates to a kind of austenitic steels of having excellent high-temperature strength, more particularly, to a kind of such as turbocharger
Or automobile exhaust system etc. is used for the heat-resistance stainless steel of high temperature, by the alloying element nickel (Ni) of costliness wherein included with low
While the alloying element of cost substitutes, additionally it is possible to realize the high temperature physical property equal to or higher than existing heat-resistance stainless steel.
Background technology
High temperature austenitic steel not only has excellent hardness, intensity, Thermomechanical Fatigue Life and fracture toughness, but also has
There is heat-staple microstructure, therefore it is used for the turbocharger of automobile or exhaust system.
Turbocharger supplies large quantity of air to improve the output of engine by being compressed to the cylinder interior of engine,
And it has following structure:It drives the turbine wheel in turbine shroud to rotate by using the exhaust gas being discharged from engine, and passes
It passs the rotary force generated when turbine wheel rotation and drives the compressor wheels rotation being used in the compression case body of the air in compressed atmosphere
Then it is supplied to engine.
Turbine shroud due to accommodating turbine wheel is constantly contacted with 800 to 900 DEG C of exhaust gas being discharged from engine, is made
Turbine shroud is obtained with the output of engine and by high thermal shock, therefore, turbine shroud needs to have at high temperature excellent
Different intensity and the performance that can continue to keep its shape.
As the material of this turbine shroud, at present using high temperature austenites such as 22 type heat-resistance stainless steels of SCH
Steel.This heat-resistance stainless steel adds the costliness of 20 weight % or more to improve the stability of austenite structure at high temperature
Alloying element Ni, this to become a reason for increasing turbine shroud manufacturing cost.
In order to solve these problems, Korean Patent Publication No. 2016-0091041 discloses one kind by comprising C:0.4
To 0.5 weight %, Si:1.0 to 2.0 weight %, Mn:1.0 to 2.0 weight %, Ni:9.0 to 12.0 weight %, Nb:1.0 extremely
2.5 weight %, W:0.5 to 3.5 weight %, remaining significantly reduce containing for Ni for the alloy of Fe and other inevitable impurity
Measure and improved by adding Nb and W the technology of castability and elevated temperature strength.
However, the Nb and W that are added to substitute Ni are not only expensive alloying element, although and in the case of Nb
Castability can be improved, but there are problems that increasing the brittleness of alloy when forming Nb carbide.
Invention content
Technical task
The object of the present invention is to provide a kind of austenitic steels, and the content by reducing Ni is manufactured with low cost, meanwhile, lead to
Cross minimize the formation of ferritic phase in microstructure and by M7C3The ratio of phase is maintained at certain level or more, in high temperature
Under excellent intensity may be implemented.
Solve project means
For solve the above subject it is an aspect of the invention to provide a kind of Ovshinskies with excellent elevated temperature strength
Body steel, it includes C:0.4 to 0.5 weight %, Si:1.0 to 2.0 weight %, Mn:5.0 to 8.0 weight %, Ni:13.5 to 16.5
Weight %, Cr:23 to 26 weight %, remaining is Fe and other inevitable impurity, and Mn contents are used as in the alloying element
With the C of the ratio of Ni contentsMn/CNiIt is maintained in the range of 0.3 to 0.9.
Invention effect
The austenitic steel of the present invention is designed by following alloy:Austenite structure is kept at high temperature, and in order to which Ni reaches
Substitute and remove Nb and W using relatively inexpensive Mn to scheduled ratio, and by minimizing the formation of ferritic phase by M7C3
The ratio of phase is maintained at certain level or more, and the elevated temperature strength at 900 DEG C is made to be up to 125MPa or more, and shape retention
It is excellent, it can be adapted for the turbine shroud of turbocharger.
In addition, compared with the austenitic steel containing 20% or more Ni, austenitic steel of the invention can save 20% with
On cost.
Description of the drawings
Fig. 1 show the embodiment of the present invention 1 and 2 and comparative example 1 to 3 austenitic steel XRD analysis result.
Fig. 2 is the microstructure photo of the embodiment of the present invention 2 and comparative example 3.
Fig. 3 shows the EDS mapping results of the microstructure photo and carbon (C) and chromium (Cr) of the embodiment of the present invention 2.
Fig. 4 shows the EDS mapping results of the microstructure photo and carbon (C) and chromium (Cr) of the comparative example 1 of the present invention.
Fig. 5 show the embodiment of the present invention 1 and 2 and the austenitic steel of comparative example 1 to 3 tension examination is carried out at 25 DEG C
The result tested.
Fig. 6 show the embodiment of the present invention 1 and 2 and the austenitic steel of comparative example 1 to 3 high temperature is carried out at 900 DEG C
The result of tensile test.
Specific implementation mode
The singulative of embodiment for describing the present invention is unless those words and phrases conclusively show opposite meaning, otherwise
Also imply that include plural form.And including meaning refer to by special characteristic, region, integer, step, action, element and/
Or ingredient embodies, it is not excluded that other special characteristics, region, integer, step, action, the presence of element, ingredient and/or group
Or addition.
Although without in addition defining, all terms used herein including technical terms and scientific terms have and this hair
The identical meaning of the bright normally understood meaning of those of ordinary skill in the art.In addition, defined in usually used dictionary
Term meets relevant technical literature and the meaning of present disclosure unless being explained further and being defined as to have, and otherwise should not be solved
It is interpreted as ideal or very formal meaning.
The present inventor exclude Nb and W etc. it is expensive and element that carbide can be formed and realization can
While bearing the elevated temperature strength of 900 DEG C or more hot environments, the result that the alloy to that can reduce Ni contents is studied is sent out
It is existing, as austenitic steel, when the content of the Ni largely added to keep austenite structure at high temperature is slightly reduced simultaneously
And in the case that Mn is substituted with estimated rate without the use of alloying elements such as Nb and W, excellent elevated temperature strength may be implemented,
To realize the present invention.
The austenitic steel of the present invention, which is characterized in that include C:0.4 to 0.5 weight %, Si:1.0 to 2.0 weight %,
Mn:5.0 to 8.0 weight %, Ni:13.5 to 16.5 weight %, Cr:23 to 26 weight %, remaining is inevitable with other for Fe
Impurity and the alloying element in Mn contents and Ni contents ratio:CMn/CNiIt is maintained in the range of 0.3 to 0.9.
The composition reason for selecting the austenitic steel of the present invention is as follows.
C:0.4 to 0.5 weight %
It is well known that C is strong austenite stabilizer element, and since solution strengthening is strong in high temperature in matrix
It plays an important role in degree.In addition to this, it by forming carbide with alloying elements such as the Cr that includes in the present invention, improves
The castability of liquid phase simultaneously improves elevated temperature strength.In order to obtain the effect of this C, the carbon of 0.4 weight % or more is needed, when it is super
When crossing 0.5 weight %, since the roughening of carbide may result in the deterioration of whole mechanical property and creep resistance, preferably
Above range.
Si:1.0 to 2.0 weight %
Si has the effect of improving high-temperature oxidation resistance, and is used as reducing agent in molten alloy.Si is anti-by helping
Only Cr aoxidizes to improve inoxidizability.The silicon oxide particle formed by Si is analysed under the overlay film formed on alloy surface by Cr
Go out, to help to form passivating film and Cr ions is inhibited to leak for no reason.This effect of Si further enhances at high temperature.When less than
When 1.0 weight %, it is difficult to the effect of the Si is fully obtained, and when Si is excessively added, since high-temperature creep resistance reduces, and
And keep austenitic matrix tissue unstable as ferrite stabilizer, therefore add 2.0 weight % or less.It is highly preferred that
The content of Si is 1.0 to 1.5 weight %.
Mn:5.0 to 9.0 weight %
Mn plays the role of austenite stabilizer element, and is similarly used as reducing agent in the melt with Si.Due to this
The austenitic steel of invention reduces Ni contents, when the content of Mn is less than 5.0 weight %, it is difficult to keep austenite structure, and work as
When more than 9.0 weight %, inoxidizability and high-temperature molding under high temperature reduce, therefore are maintained at 9.0 weight % or less.It is more excellent
The content of selection of land, Mn is 5.5 to 8.0 weight %.
Ni:13.5 to 16.5 weight %
Ni is to improve the various mechanical properties comprising toughness, corrosion resistance and anti-oxidant as austenite stabilizer element
Property indispensable element reduce elevated temperature strength and when less than 13.5 weight %, therefore not preferably, and when more than 16.5 weight %
When, so that the effect of reduction manufacturing cost is reduced, therefore not preferably.
Cr:23 to 26 weight %
Inoxidizability excellent as stainless steel Cr and corrosion proof most important element form Cr2O3 shapes in alloy surface
The passivating film of the stabilization of state, to improve corrosion resistance.The content of Cr is higher, and corrosion resistance is stronger, and also contributes under high temperature
Inoxidizability and corrosion resistance.In order to improve corrosion resistance, Cr preferably adds 23 weight % or more, and Cr is as ferrite stabilization member
Element can form ferritic phase when being excessively added, so as to form a large amount of carbide, therefore be limited in 26 weight % with
Under.
The ratio of Mn contents and Ni contents, CMn/CNi0.3 to 0.9
When the ratio of Mn contents and Ni contents is less than 0.3 in the alloying element, Ni replacements amount is insufficient and economy
It is not high, and when more than 0.9, excellent elevated temperature strength cannot be obtained, therefore not preferably.Preferred range is 0.3 to 0.6.
In addition, tensile strength of the austenitic steel at 900 DEG C of the present invention is 125MPa or more, preferably 128MPa with
On, more preferably 130MPa or more.
P:0.04 weight % or less
P is inevitably to be used as the mixed ingredient of impurity, and P may be segregated and be produced to the physical property of alloy in the alloy
Raw negative effect, therefore 0.04 weight % is preferably remained in hereinafter, it is highly preferred that 0.03 weight % or less.
S:0.04 weight % or less
S forms such as that MnS sulfides are to improve the machinability of alloy in the alloy, still, since sulfide reduces
The overall performance of alloy, therefore preferably remain in 0.04 weight % or less.
In addition, the austenitic steel of the present invention is preferably indicated by following formula 1 to stably keep austenite structure at high temperature
NieqFor 31 to 32, the Cr that is indicated by following formula 2eqIt is 25 to 28.
[Formula 1]
Nieq=%Ni+30%C+0.87%Mn-0.33%Cu+30 (%N-0.045)
[Formula 2]
Creq=%Cr+%Mo+%W+1.5%Si+0.5%Nb+5%V+3%Al
In addition, the present invention austenitic steel, when ferritic structure in microstructure ratio with area ratio be 1% or more
When, stability is reduced at high temperature, therefore not preferably, due to M7C3Mutually play the role of improving room temperature and elevated temperature strength, therefore excellent
It is selected as 2% or more, but in order to increase M7C3The area ratio of phase and increase Mn contents, then can increase the area ratio of ferritic phase, therefore
M7C3The area of phase is than preferably 2 to 3%.
[Shi Shili ]
The following table 1 shows the embodiment 1 of austenitic steel of the present invention, embodiment 2 and in order to change compared with embodiment
Become the comparative example 1 of the ratio of Ni and Mn, the composition of comparative example 2 and comparative example 3.
Table 1
5 kinds of raw materials with composition as shown above are prepared, after then being dissolved in melting furnace, at 1550 DEG C to 1600
It comes out of the stove at DEG C, and is injected into cylindrical shape test film casting mold at 1500 DEG C to 1550 DEG C to obtain test film immediately.
Facies analysis is carried out using XRD and EBSD (electron backscatter diffraction) to thus obtained test film, use is micro-
Mirror and EDS have carried out Analysis on Microstructure, and have carried out tensile test under room temperature (25 DEG C) and high temperature (900 DEG C) and measured
Phase fraction.
Microstructure
Fig. 1 show the embodiment of the present invention 1 and 2 and comparative example 1 to 3 austenitic steel XRD analysis result.Fig. 2
It is the microstructure photo of the embodiment of the present invention 2 and comparative example 3, Fig. 3 shows that the microstructure of the embodiment of the present invention 2 is shone
Piece and the EDS of carbon (C) and chromium (Cr) mapping as a result, Fig. 4 show the present invention comparative example 1 microstructure photo and carbon
(C) and the EDS mapping results of chromium (Cr).
As shown in Figure 1, the peak value of ferritic phase is not detected in comparative example 1, comparative example 2, embodiment 1 and embodiment 2,
And the peak value of ferritic phase is partly detected in comparative example 3.
As the following table 2 shows ferritic phase and M7C3 phases in the microstructure for measuring steel as shown in Figures 3 and 4 using EBSD
The result of shared score.
Table 2
As shown in upper table 2, the embodiment of the present invention 1 is not shown ferritic phase, and as shown in Fig. 2, embodiment 2 the case where
Under, detect 0.1% minimal amount of ferrite below.
Although Ni and Mn does not have the effect for the carbide forming agent for directly forming carbide, as shown in upper table 2, with
The replacement amount of Mn increases, M7C3The score of phase tends to increase.Due to M7C3Mutually play the role of improving room temperature and elevated temperature strength, because
This is conducive to improve elevated temperature strength.However, as shown in comparative example 3, when the content of Mn increases, ferritic phase increase makes austenite
The stability of phase reduces, to make the impatient acute deterioration of high temperature substrate.It is therefore preferable that inhibiting below 1% (preferably by ferritic phase
Be 0.1% or less) while increase M7C3The score of phase.
Room temperature and Testing Tensile Strength at Elevated Temperature
Fig. 5 show the embodiment of the present invention 1 and 2 and the austenitic steel of comparative example 1 to 3 tension examination is carried out at 25 DEG C
It is testing as a result, Fig. 6 show the embodiment of the present invention 1 and 2 and the austenitic steel of comparative example 1 to 3 high temperature is carried out at 900 DEG C
The result of tensile test.
As the following table 3 shows the tensile test result of Figures 5 and 6.
Table 3
As shown in table 3, compared with the comparative example 2 of the comparative example 1 of the Ni containing 20 weight % and Ni containing 18 weight %,
The embodiment of the present invention 1 and embodiment 2 show same or higher room temperature tensile strength and under elevated temperature tensile characteristics
Show identical characteristic.
In contrast to this, in the case where Ni contents are comparative example 3 of 12 weight %, although room temperature tensile strength is very high,
But Testing Tensile Strength at Elevated Temperature significantly reduces, therefore is not suitable for needing the turbine with durability at 900 DEG C or more of temperature to increase
The shell of depressor.
Especially compared with comparative example 1, Ni contents can reduced by 4 to 6% by the austenitic steel of embodiment of the present invention
While keep elevated temperature tensile characteristic in same level above, to be realized with a low cost excellent hot properties.
Claims (7)
1. a kind of austenitic steel of having excellent high-temperature strength, it includes C:0.4 to 0.5 weight %, Si:1.0 to 2.0 weight %, Mn:
5.0 to 8.0 weight %, Ni:13.5 to 16.5 weight %, Cr:23 to 26 weight %, remaining is inevitably miscellaneous with other for Fe
Matter,
The ratio of Mn contents and Ni contents, C in the alloying elementMn/CNiIt is maintained in the range of 0.3 to 0.9.
2. the austenitic steel of having excellent high-temperature strength as described in claim 1, wherein P is 0.04 weight % in the impurity
Below, S is 0.04 weight % or less.
3. the austenitic steel of having excellent high-temperature strength as described in claim 1, wherein at 900 DEG C, tensile strength 125MPa
More than.
4. the austenitic steel of having excellent high-temperature strength as described in claim 1, wherein the austenitic steel by Xia [Formula 1]Table
The Ni showneqFor 31 to 32, by Xia [Formula 2]The Cr of expressioneqIt is 25 to 28:
[Formula 1]
Nieq=%Ni+30%C+0.87%Mn-0.33%Cu+30 (%N-0.045)
[Formula 2]
Creq=%Cr+%Mo+%W+1.5%Si+0.5%Nb+5%V+3%Al.
5. the austenitic steel of having excellent high-temperature strength as described in claim 1, wherein the iron element for including in the austenitic steel
Body tissue is less than 1% with area ratio.
6. the austenitic steel of having excellent high-temperature strength as claimed in claim 5, wherein the M for including in the austenitic steel7C3
Mutually with area ratio for 2 to 3%.
7. a kind of turbine shroud is made of the austenitic steel described in any one in claim 1 to 6.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR10-2016-0158429 | 2016-11-25 | ||
| KR1020160158429A KR101809853B1 (en) | 2016-11-25 | 2016-11-25 | Austenitic steel excellent in high temperature strength |
| PCT/KR2017/013371 WO2018097604A1 (en) | 2016-11-25 | 2017-11-22 | Austenitic steel with excellent high-temperature strength |
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| Publication Number | Publication Date |
|---|---|
| CN108699661A true CN108699661A (en) | 2018-10-23 |
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| CN201780014102.0A Pending CN108699661A (en) | 2016-11-25 | 2017-11-22 | The austenitic steel of having excellent high-temperature strength |
Country Status (3)
| Country | Link |
|---|---|
| KR (1) | KR101809853B1 (en) |
| CN (1) | CN108699661A (en) |
| WO (1) | WO2018097604A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113695519A (en) * | 2021-08-30 | 2021-11-26 | 西峡飞龙特种铸造有限公司 | Steel casting process |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US11414734B2 (en) | 2018-09-25 | 2022-08-16 | Garrett Transportation I Inc | Austenitic stainless steel alloys and turbocharger kinematic components formed from stainless steel alloys |
| CN111041386B (en) * | 2018-10-12 | 2022-07-29 | 博格华纳公司 | Austenitic alloy for turbocharger |
| US11655527B2 (en) * | 2020-07-01 | 2023-05-23 | Garrett Transportation I Inc. | Austenitic stainless steel alloys and turbocharger kinematic components formed from stainless steel alloys |
| CN115213352B (en) * | 2022-08-12 | 2024-02-02 | 肇庆匹思通机械有限公司 | Volute forming process |
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| EP0097106A1 (en) * | 1982-05-26 | 1983-12-28 | Ugine Savoie | Heat resisting cast steel, abrasion-proof and able to withstand strain at very high temperatures in atmospheres containing sulfur oxides |
| CN1156187A (en) * | 1995-11-27 | 1997-08-06 | 扬州市永进泵阀厂 | Novel anti-corrosion wear-resistance stainless steel and its producing process |
| CN102086498A (en) * | 2009-12-04 | 2011-06-08 | 沈阳鑫火铸造有限公司 | High-Cr high-Ni anti-oxidation heat resistant steel |
| CN102159744A (en) * | 2009-06-24 | 2011-08-17 | 日立金属株式会社 | Heat-resistant steel for engine valve having excellent high-temperature strength |
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| JPH05148591A (en) * | 1991-11-27 | 1993-06-15 | Aichi Steel Works Ltd | Steel for discharge valve excellent in grinding property |
| JPH11323479A (en) * | 1998-05-13 | 1999-11-26 | Toyota Central Res & Dev Lab Inc | Heat resistant cast steel |
| KR100428572B1 (en) | 1999-12-09 | 2004-04-28 | 주식회사 포스코 | A heat resistant stainless steel having superior oxidizing resistant and heat resistant strength |
| KR100766251B1 (en) | 2006-06-09 | 2007-10-12 | 주식회사 포스코 | Ni saving heat resistant austenitic stainless steel with excellent high temperature properties |
| JP6046591B2 (en) | 2013-03-22 | 2016-12-21 | トヨタ自動車株式会社 | Austenitic heat-resistant cast steel |
-
2016
- 2016-11-25 KR KR1020160158429A patent/KR101809853B1/en active IP Right Grant
-
2017
- 2017-11-22 WO PCT/KR2017/013371 patent/WO2018097604A1/en active Application Filing
- 2017-11-22 CN CN201780014102.0A patent/CN108699661A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0097106A1 (en) * | 1982-05-26 | 1983-12-28 | Ugine Savoie | Heat resisting cast steel, abrasion-proof and able to withstand strain at very high temperatures in atmospheres containing sulfur oxides |
| CN1156187A (en) * | 1995-11-27 | 1997-08-06 | 扬州市永进泵阀厂 | Novel anti-corrosion wear-resistance stainless steel and its producing process |
| CN102159744A (en) * | 2009-06-24 | 2011-08-17 | 日立金属株式会社 | Heat-resistant steel for engine valve having excellent high-temperature strength |
| CN102086498A (en) * | 2009-12-04 | 2011-06-08 | 沈阳鑫火铸造有限公司 | High-Cr high-Ni anti-oxidation heat resistant steel |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113695519A (en) * | 2021-08-30 | 2021-11-26 | 西峡飞龙特种铸造有限公司 | Steel casting process |
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| WO2018097604A1 (en) | 2018-05-31 |
| KR101809853B1 (en) | 2017-12-26 |
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