WO2013104357A1 - Rostfreier ferritischer stahl und verfahren zur herstellung eines hochtemperaturbauteils - Google Patents
Rostfreier ferritischer stahl und verfahren zur herstellung eines hochtemperaturbauteils Download PDFInfo
- Publication number
- WO2013104357A1 WO2013104357A1 PCT/DE2013/100005 DE2013100005W WO2013104357A1 WO 2013104357 A1 WO2013104357 A1 WO 2013104357A1 DE 2013100005 W DE2013100005 W DE 2013100005W WO 2013104357 A1 WO2013104357 A1 WO 2013104357A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- max
- steel
- temperature
- mass
- niobium
- Prior art date
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Classifications
-
- 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
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Definitions
- the invention relates to a stainless, ferritic steel, a high-temperature component made of this material and a method for producing a Hocbtemperaturbauteils.
- High-temperature components are usually made of stainless, ferritic stainless steels, inter alia on the basis of steel grades with the names DiN EN 1 .4509 or 1, 4521.
- DiN EN 1 .4509 or 1, 4521 DiN EN 1 .4509 or 1, 4521.
- Hochtemperafurbaumaschinener in the context of the invention are in particular exhaust gas leading components to understand, in particular exhaust manifold and Aufiademaschinen, such as, turbocharger or pressure loader.
- Exhaust manifolds are operated in a temperature range between 250 ° and 850 ° C (with a variation range of + 1-100 ° C).
- Turbochargers are subject to even higher Temperaturbeiastungen. They are partly operated at maximum temperatures of 1 .100 ° C +! ⁇ 50 ° C.
- the materials mentioned have sufficiently high creep strengths at typical exhaust gas temperatures between 25CTC and 850 ° C. whereby they are suitable for use at such high temperatures.
- the hot tensile strength at a temperature between 800 ° C and 90 ⁇ ° C is the steel grade with the label 1 .4509 on the order of 80 MPa hei 800 Ü C to 23 MPa at 900 ° C.
- the invention is therefore based on the object to show a stainless ferritic steel, which has a high temperature resistance, and to show a high-temperature component of such a material.
- a method for producing a Hocbtemperaturhauteils be demonstrated from this material, wherein the Hochtemperaturbautei! characterized by high temperature resistance.
- thermomechanical properties are to be understood as those superior to grade 1.4509.
- the ferritic stainless steel of the present invention has either of the following alloy components (in mass%);
- Co Co + 0.1
- Fe remainder iron
- impurities caused by agglomeration, wherein the structure has a grain diameter of 12 m to 80 ⁇
- inventive stainless ferritic steel gives the following alloy components (in mass percent):
- Remainder iron (Fe) and impurities caused by the melt the structure having a grain diameter of 12 m to 80 pm.
- alloys are characterized first by the fact that the sum of the alloying parts minima! is held.
- the alloys are distinguished by the Laves phase formation described below, which results in optimum high-temperature properties, ie especially for a cyclic application with temperatures of 250 ° to 950 ° C.
- the creep times (tk) are at the specification of a tensile stress of 23 MPa and a temperature of 850 ° C with t k £ 4h significantly over 10% higher compared to the steel grade 1 .4509.
- the thermocycling experiments showed a comparable tendency
- the grain diameter is in a range of 12 pm and 80 pm corresponding to a grain size number of 4 to 10 according to AST E 1 12.
- the grain diameter is in a range of 30 pm and 80 pm according to AST 5 to 7. More preferably, the grain diameter is 35 pm according to AST 7.
- the alloy compositions have a decisive influence on the desired high-temperature properties. Desirable high-temperature properties are to be understood as those which are superior to the steel material 1 .4509.
- the hot tensile strength at a temperature of 900 ° C should be greater than 28 Pa. It preferably moves on the order of 30 MPa to 45 MPa.
- Laves phases are intermetallic compounds. These intermetallic compounds are formed by the addition of niobium.
- the addition of silicon favors the formation of the Lavesphase.
- the alloying of tungsten or molybdenum (X content of Fe 2 X) is used, inter alia, for mixed crystal solidification. The superposition of the two effects leads to an improvement in the high-temperature property of the material.
- the Laves phase has an influence on the improvement of creep resistance. Although it is known from the scope of the fuel cell to use ferritic stainless steels, but only in connection with rare earths such as lanthanum. This is it very costly alloying components whose use is avoided for economic reasons in the invention.
- Lavesphasen With the alloy according to the invention, which receives both molybdenum, tungsten and niobium in combination with silicon, Lavesphasen can be formed to the desired extent, which are also present at temperatures above 850 ° C.
- the sum of the mass fractions of tungsten and molybdenum is in particular smaller than the sum of the mass fractions of silicon and niobium + 2.5%.
- the overall result is improved creep strength aimed for high temperature applications.
- nickel has the function of increasing the strength and yield strength of the alloy.
- MnS manganese sulphides
- FeS contributes to a strong weakening of the grain boundaries, The reduction of FeS thus leads to the desired strengthening of grain boundaries.
- Niobium has a decisive influence on the Laves phase formation (Fe 2 Nb). As a result, stainless ferritic stainless steels containing niobium tend to resonate. The C content is crucial because Nb has a high affinity to C. If the C content is not low enough, no Laves phase is formed, but NbC. However, the Lewes phase can dissolve at higher temperatures (T> 800 ° C), which may decrease the creep resistance. This in turn depends on the alloy composition and thus on the solvus temperature of the Lavesphase. However, the interaction with the alloying elements mentioned below means that finest Laves phases and, to a small extent, carbides also form within the grain and also do not dissolve at higher temperatures.
- the interaction provides both grain consolidation and improved grain boundary cohesion.
- Carbon contained in stabilized ferritic stainless steels in the typical order of magnitude C ⁇ 0.025% provides, in particular, for the formation of Ti, Nb carbides, which can serve as nuclei and stabilize the microstructure, within the stated limits.
- silicon serves to stabilize the Lavesphase. Ab initio calculations and thermodynamic calculations show that Si-AnteH promotes Laves phase expansion. It can thereby be achieved that the Lavesphase is maintained even at higher temperatures in a range of T - 900 ° to T ⁇ 950 ° C. A maximum of 0.08 to 0.9% silicon is the optimum range for stabilizing the Laves phase. If the Si component is too high, then the solvus temperature of the Laves phase can be shifted to higher temperatures so that the Laves phases are coarsely separated during production and can no longer be dissolved.
- the steel is preferably partially Ti stabilized to increase the level of dissolved Nb. Since C and N are partially ligated, essentially free Nb and Si are left as free variables with an influence on the Laves phase.
- % Nb -0.25 (% Si + 0.65 (% Si) 2 - 0.75 (% Si) + 1
- the steel sheet is heated with the composition described above to a temperature which is between 400 "C and at most 50 ° C above the Rekalailisationstemperatur held for 5 min to 5 h in this temperature range
- the microstructure has a grain diameter of 12 ⁇ m to 80 ⁇ m, corresponding to approximately AST 4 to AST 10,
- the grain diameter is between 30 ⁇ m and 60 ⁇ m in accordance with ASTIV15 to ASTM7.
- the grain diameter is corresponding to 35 ⁇ m ASTM 7.
- the microstructure also has Laves phase Fe 2 X, wherein X represents at least one alloying element selected from the group comprising Nb, W, or Mo.
- Solution heat treatment at elevated temperature, during which recovery and recrystallization can take place causes niobium to dissolve.
- niobium will go into solution.
- the particle size will be adjusted.
- the Rekristallisationsglübung takes place at about 1150 ° C and is highly dependent on the alloy composition, the degree of deformation and especially the presence of a second phase (Laves, MX, etc.).
- the material is heated to a temperature above 400 ° C to a maximum of 50 ° above the recrystallization temperature.
- the minimum temperature of the heating is 200 "below the recrystallization temperature, in which the material is held for a certain period of time, and may be between 5 minutes and 5 hours.
- the grain diameter is usually ASTM8 or ASTM9
- the cold forming is therefore usually followed by a solution annealing process to the desired grain size and the desired structure even in the cold formed Bauteli to reach,
- the invention thus relates to a Lavesphase reinforced ferritic chromium steel, which obtains a higher heat resistance by the combined addition of Mo and W and this can remain for a long period due to the obstruction of grain growth by stable Lavesphase at T> 900 ° C, while others o would neutralize W-glazed ferrites without Laves phase by coarsening.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE112013000549.2T DE112013000549B4 (de) | 2012-01-13 | 2013-01-10 | Rostfreier ferritischer Stahl und Verfahren zur Herstellung eines Hochtemperaturbauteils |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102012100289A DE102012100289A1 (de) | 2012-01-13 | 2012-01-13 | Rostfreier ferritischer Stahl und Verfahren zur Herstellung eines Hochtemperaturbauteils |
DE102012100289.4 | 2012-01-13 |
Publications (1)
Publication Number | Publication Date |
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WO2013104357A1 true WO2013104357A1 (de) | 2013-07-18 |
Family
ID=47632654
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/DE2013/100005 WO2013104357A1 (de) | 2012-01-13 | 2013-01-10 | Rostfreier ferritischer stahl und verfahren zur herstellung eines hochtemperaturbauteils |
Country Status (2)
Country | Link |
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DE (2) | DE102012100289A1 (de) |
WO (1) | WO2013104357A1 (de) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020051722A1 (zh) * | 2018-09-13 | 2020-03-19 | 安徽霍山科皖特种铸造有限责任公司 | 一种冶金材料及利用该材料制造冶金导卫某零件的方法 |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018022950A1 (en) | 2016-07-28 | 2018-02-01 | Borgwarner Inc. | Ferritic steel for turbochargers |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1170392A1 (de) * | 2000-07-04 | 2002-01-09 | Kawasaki Steel Corporation | Ferritischer rostfreier Stahl |
US20090092513A1 (en) * | 2007-02-26 | 2009-04-09 | Junichi Hamada | Ferritic Stainless Steel Sheet Superior in Heat Resistance |
EP2112245A1 (de) * | 2007-02-02 | 2009-10-28 | Nisshin Steel Co., Ltd. | Ferritischer nichtrostender stahl für abgaspassagenbauelement |
EP2166120A1 (de) * | 2008-03-07 | 2010-03-24 | JFE Steel Corporation | Ferritischer edelstahl mit hervorragender hitzebeständigkeit |
US20100122800A1 (en) * | 2008-11-14 | 2010-05-20 | Yukihiro Nishida | Ferritic stainless steel and steel sheet for heat pipes, and heat pipe and high-temperature exhaust heat recovery system |
Family Cites Families (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3064871B2 (ja) | 1995-06-22 | 2000-07-12 | 川崎製鉄株式会社 | 成形加工後の耐肌あれ性および高温疲労特性に優れるフェライト系ステンレス熱延鋼板 |
-
2012
- 2012-01-13 DE DE102012100289A patent/DE102012100289A1/de not_active Withdrawn
-
2013
- 2013-01-10 WO PCT/DE2013/100005 patent/WO2013104357A1/de active Application Filing
- 2013-01-10 DE DE112013000549.2T patent/DE112013000549B4/de active Active
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1170392A1 (de) * | 2000-07-04 | 2002-01-09 | Kawasaki Steel Corporation | Ferritischer rostfreier Stahl |
EP2112245A1 (de) * | 2007-02-02 | 2009-10-28 | Nisshin Steel Co., Ltd. | Ferritischer nichtrostender stahl für abgaspassagenbauelement |
US20090092513A1 (en) * | 2007-02-26 | 2009-04-09 | Junichi Hamada | Ferritic Stainless Steel Sheet Superior in Heat Resistance |
EP2166120A1 (de) * | 2008-03-07 | 2010-03-24 | JFE Steel Corporation | Ferritischer edelstahl mit hervorragender hitzebeständigkeit |
US20100122800A1 (en) * | 2008-11-14 | 2010-05-20 | Yukihiro Nishida | Ferritic stainless steel and steel sheet for heat pipes, and heat pipe and high-temperature exhaust heat recovery system |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020051722A1 (zh) * | 2018-09-13 | 2020-03-19 | 安徽霍山科皖特种铸造有限责任公司 | 一种冶金材料及利用该材料制造冶金导卫某零件的方法 |
Also Published As
Publication number | Publication date |
---|---|
DE112013000549A5 (de) | 2014-11-06 |
DE112013000549B4 (de) | 2023-06-22 |
DE102012100289A1 (de) | 2013-07-18 |
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