EP0255597A2 - Low alloy steels - Google Patents
Low alloy steels Download PDFInfo
- Publication number
- EP0255597A2 EP0255597A2 EP87109046A EP87109046A EP0255597A2 EP 0255597 A2 EP0255597 A2 EP 0255597A2 EP 87109046 A EP87109046 A EP 87109046A EP 87109046 A EP87109046 A EP 87109046A EP 0255597 A2 EP0255597 A2 EP 0255597A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- steels
- temperatures
- joules
- fine grain
- related impurities
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Definitions
- the invention relates to microalloyed pearlitic steels as a material for molded parts, which are preferably obtained by massive forming by forging in a die at high temperatures.
- the invention has for its object to provide steels which have a high fine grain resistance up to temperatures of 1300 ° C and thus in combination high strength and high toughness in large-scale production.
- the microalloyed pearlitic steels according to the invention have the following composition: 0.20 to 0.50%. C, 0.40 to 1.0% Si, 0.80 to 1.80% Mn, 0.008 to 0.2% S, 0 to 0.7% Cr, 0 to 0.1% Al, 0 to 0, 04% N, 0.01 to 0.05% Ti, remainder iron and melting-related impurities, whereby mixed sulfides (manganese, titanium carbonitrides and the like) are excreted on the grain boundaries.
- mixed sulfides mangaganese, titanium carbonitrides and the like
- up to 0.20% V and / or 0.10% Nb can additionally be contained in the steel.
- Such steels can solidify at a solidification rate in the range of 3 to 25 mm / min so that sulfides are separated out in finely divided form between the liquidus and solidus temperatures.
- the fine distribution This phase is responsible for the high fine grain resistance and the resulting combination of high strength and high toughness (Fig. 1).
- a steel is preferably selected from the following range: 0.20 to 0.35% C, 0.50 to 0.80% Si, 1.00 to 1.70% Mn, 0.01 to 0.09% S, 0 , 20 to 0.50% Cr, 0.015 to 0.06% Al, 0.015 to 0.030% N, 0.05 to 0.15% V and / or 0.02 to 0.10% Nb, 0.01 to 0 , 04% Ti, remainder iron including impurities due to melting.
- the steels according to the invention are therefore outstandingly suitable for use in automotive components.
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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 Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Laminated Bodies (AREA)
- Acyclic And Carbocyclic Compounds In Medicinal Compositions (AREA)
- Heat Treatment Of Articles (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Liquid Crystal Substances (AREA)
Abstract
Description
Die Erfindung bezieht sich auf mikrolegierte perlitische Stähle als Werkstoff für Formteile, die vorzugsweise durch Massivumformung durch Schmieden im Gesenk bei hohen Temperaturen erhalten werden.The invention relates to microalloyed pearlitic steels as a material for molded parts, which are preferably obtained by massive forming by forging in a die at high temperatures.
Aus dem Schrifttum ist die Wirkung einer feinen Dispersion von Titannitriden in geringer Konzentration auf die Beständigkeit gegen Kornwachstum bekannt (C.J. Cuddy, J.C. Raley: "Austenite Grain Coarsening in Microalloyed Steels", Mettallgurgical Trans. A, Vol. 14 A, Oct. 1983, S. 1989 - 1995). Eine großtechnische Nutzung dieser Wirkung ist jedoch kaum möglich, da bei üblichen Erstarrungsgeschwindigkeiten der Temperaturbereich zwischen Liquids- und Solidustemperatur zu langsam durchlaufen wird.The effect of a fine dispersion of titanium nitrides in low concentration on the resistance to grain growth is known from the literature (CJ Cuddy, JC Raley: "Austenite Grain Coarsening in Microalloyed Steels", Mettallgurgical Trans. A, Vol. 14 A, Oct. 1983, Pp. 1989 - 1995). However, this effect can scarcely be used on an industrial scale, since the temperature range between liquids and solidus temperatures is too slow for normal solidification speeds.
Der Erfindung liegt die Aufgabe zugrunde, Stähle zu schaffen, die auch bei großtechnischer Erzeugung eine hohe Feinkornbeständigkeit bis zu Temperaturen von 1300°C und damit in Kombination hohe Festigkeit und hohe Zähigkeit aufweisen.The invention has for its object to provide steels which have a high fine grain resistance up to temperatures of 1300 ° C and thus in combination high strength and high toughness in large-scale production.
Die erfindungsgemäßen mikrolegierten perlitischen Stähle haben folgende Zusammensetzung: 0,20 bis 0,50 %. C, 0,40 bis 1,0 % Si, 0,80 bis 1,80 % Mn, 0,008 bis 0,2 % S, 0 bis 0,7 % Cr, 0 bis 0,1 % Al, 0 bis 0,04 % N, 0.01 bis 0,05 % Ti, Rest Eisen und erschmelzungsbedingte Verunreinigungen, wobei auf den Korngrenzen Mischsulfide (Mangan-, Titankarbonitride u.dgl.) ausgeschieden sind. Bevorzugt können zusätzlich bis 0,20 % V und/oder 0,10 % Nb im Stahl enthalten sein.The microalloyed pearlitic steels according to the invention have the following composition: 0.20 to 0.50%. C, 0.40 to 1.0% Si, 0.80 to 1.80% Mn, 0.008 to 0.2% S, 0 to 0.7% Cr, 0 to 0.1% Al, 0 to 0, 04% N, 0.01 to 0.05% Ti, remainder iron and melting-related impurities, whereby mixed sulfides (manganese, titanium carbonitrides and the like) are excreted on the grain boundaries. Preferably up to 0.20% V and / or 0.10% Nb can additionally be contained in the steel.
Solche Stähle können bei einer Erstarrungsgeschwindigkeit im Bereich von 3 bis 25 mm/min so erstarren, daß dabei zwischen Liquidus- und Solidustemperatur Sulfide in feinverteilter Form ausgeschieden werden. Die Feinverteilung dieser Phase ist für die hohe Feinkornbeständigkeit und die dadurch bedingte Kombination von hoher Festigkeit und hoher Zähigkeit verantwortlich (Bild 1).Such steels can solidify at a solidification rate in the range of 3 to 25 mm / min so that sulfides are separated out in finely divided form between the liquidus and solidus temperatures. The fine distribution This phase is responsible for the high fine grain resistance and the resulting combination of high strength and high toughness (Fig. 1).
Vorzugsweise wird ein Stahl aus folgendem Bereich ausgewählt: 0,20 bis 0,35 % C, 0,50 bis 0,80 % Si, 1,00 bis 1,70 % Mn, 0,01 bis 0,09 % S, 0,20 bis 0,50 % Cr, 0,015 bis 0,06 % Al, 0,015 bis 0,030 % N, 0,05 bis 0,15 % V und/oder 0,02 bis 0,10 % Nb, 0,01 bis 0,04 % Ti, Rest Eisen einschließlich erschmelzungsbedingter Verunreinigungen.A steel is preferably selected from the following range: 0.20 to 0.35% C, 0.50 to 0.80% Si, 1.00 to 1.70% Mn, 0.01 to 0.09% S, 0 , 20 to 0.50% Cr, 0.015 to 0.06% Al, 0.015 to 0.030% N, 0.05 to 0.15% V and / or 0.02 to 0.10% Nb, 0.01 to 0 , 04% Ti, remainder iron including impurities due to melting.
Es wurde festgestellt, daß nur Stähle der beanspruchten Zusammensetzung bis zu Verformungstemperaturen oder Glühtemperaturen von 1300°C eine hohe Feinkornbeständigkeit besitzen (s. Bilder 1 und 2). Anhand der in den Tafeln 2 und 3 aufgeführten Beispiele wird deutlich, daß von den Stählen (Zusammensetzung siehe Tafel 1)nur die erfindungsgemäßen Stähle F und G die hervorragende Kombination von hoher Festigkeit und hoher Zähigkeit zeigen. Diese Stähle weisen eine Zugfestigkeit von mindestens 800 N/mm2, eine 0,2 %-Dehngrenze von mindestens 550 N/mm2 bei Bruchverformbarkeitskennwerten von mindestens 15 % Bruchdehnung (10 = 5 d ) und mindestens 45 % Brucheinschnürung auf. Die bei Raumtemperatur an DVM-Proben ermittelten Werte der Kerbschlagarbeit betragen mindestens 35 Joule. Die Vergleichsstähle A bis E ohne Titan haben zwar auch hohe Festigkeit, s. Tafel 2, aber unzureichende Zähigkeit von unter 30 Joule, s. Tafel 3.It was found that only steels of the claimed composition up to deformation temperatures or annealing temperatures of 1300 ° C have a high fine grain resistance (see Figures 1 and 2). On the basis of the examples listed in Tables 2 and 3, it is clear that of the steels (for composition, see Table 1) only the steels F and G according to the invention show the excellent combination of high strength and high toughness. These steels have a tensile strength of at least 800 N / mm 2 , a 0.2% proof stress of at least 550 N / mm 2 with fracture deformability values of at least 15% elongation at break (1 0 = 5 d) and at least 45% fracture necking. The notched bar impact work values determined at room temperature on DVM samples are at least 35 joules. The comparative steels A to E without titanium also have high strength, see Table 2, but insufficient toughness of less than 30 joules, see Table 3.
Bevorzugt werden auch Stähle aus folgendem Bereich:
- 0,35 bis 0,45 % C, 0,5 bis 0,8 % Si, 1,0 bis 1,7 % Mn,
- 0,01 bis 0,09 % S, 0,2 bis 0,5 % Cr, 0,015 bis 0,06 % Al, 0,015 bis 0,030 % N, 0,05 bis 0,15 % V und/oder 0,02 bis
- 0,10 % Nb, 0,01 bis 0,04 % Ti, Rest Eisen einschließlich erschmelzungsbedingter Verunreinigungen.
- 0.35 to 0.45% C, 0.5 to 0.8% Si, 1.0 to 1.7% Mn,
- 0.01 to 0.09% S, 0.2 to 0.5% Cr, 0.015 to 0.06% Al, 0.015 to 0.030% N, 0.05 to 0.15% V and / or 0.02 to
- 0.10% Nb, 0.01 to 0.04% Ti, balance iron including melting-related impurities.
Es wurde festgestellt, daß auch diese Stähle bis zu Verformungstemperaturen oder Glühtemperaturen von 1300°C eine hohe Feinkornbeständigkeit besitzen (s. Bild 3). Anhand der in den Tafeln 4 bis 6 aufgeführten Beispiele (Zusammensetzungen in Tafel 4) wird deutlich, daß nur die erfindungsgemäßen Stähle I und J die hervorragende Kombination von hoher Festigkeit und hoher Zähigkeit aufweisen. Diese Stähle weisen eine Zugfestigkeit von mindestens 850 N/mm2, eine 0,2 %-Dehngrenze von mindestens 600 N/mm2 bei Bruchverformbarkeitskennwerten von mindestens 12 % Bruchdehnung (1o = 5 do) und mindestens 40 % Brucheinschnürung bei einer Kerbschlagarbeit bei Raumtemperatur von mindestens 30 Joule an DVM-Pröben auf. Der Stahl 4 ohne Titan erweist sich dagegen mit Werten unter 22 Joule als nicht ausreichend zäh.It was found that these steels also have a high resistance to fine grains up to deformation temperatures or annealing temperatures of 1300 ° C (see Fig. 3). From the examples listed in Tables 4 to 6 (compositions in Table 4) it is clear that only the steels I and J according to the invention have the outstanding combination of high strength and high toughness. These steels have a tensile strength of at least 850 N / mm 2 , a 0.2% proof stress of at least 600 N / mm 2 with fracture deformability values of at least 12% elongation at break (1 o = 5 d o ) and at least 40% fracture necking when notched at room temperature of at least 30 joules on DVM samples. Steel 4 without titanium, on the other hand, proves to be insufficiently tough with values below 22 joules.
Auch diese Kombination von noch höherer Festigkeit bei guter Zähigkeit von mindestens 30 Joule ist bei einem mikrolegierten perlitischen Stahl ungewöhnlich.This combination of even higher strength with good toughness of at least 30 joules is unusual for a micro-alloyed pearlitic steel.
Die erfindungsgemäßen Stähle sind daher in hervorragender Weise für den Einsatz für Automobil-Bauteile geeignet.The steels according to the invention are therefore outstandingly suitable for use in automotive components.
Eigenschaften über den gesamten Querschnitt bis zum KernProperties across the entire cross-section down to the core
Abmessungen der Stähle: 50 mm Durchmesser
Eigenschaften über den gesamten Querschnitt bis zum KernProperties across the entire cross-section down to the core
Abmessungen der Stähle: 50 mm Durchmesser
Claims (5)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT87109046T ATE70567T1 (en) | 1986-07-05 | 1987-06-24 | MICROALLOY STEELS. |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE3622735 | 1986-07-05 | ||
DE3622735 | 1986-07-05 | ||
DE3719569 | 1987-06-12 | ||
DE3719569A DE3719569C2 (en) | 1986-07-05 | 1987-06-12 | Microalloyed steels. |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0255597A2 true EP0255597A2 (en) | 1988-02-10 |
EP0255597A3 EP0255597A3 (en) | 1989-01-11 |
EP0255597B1 EP0255597B1 (en) | 1991-12-18 |
Family
ID=25845343
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP87109046A Expired - Lifetime EP0255597B1 (en) | 1986-07-05 | 1987-06-24 | Low alloy steels |
Country Status (8)
Country | Link |
---|---|
US (1) | US4838963A (en) |
EP (1) | EP0255597B1 (en) |
KR (1) | KR880003023A (en) |
AT (1) | ATE70567T1 (en) |
DE (2) | DE3719569C2 (en) |
ES (1) | ES2027998T3 (en) |
FI (1) | FI88625B (en) |
GR (1) | GR3003399T3 (en) |
Families Citing this family (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE4014072A1 (en) * | 1989-06-09 | 1990-12-20 | Thyssen Edelstahlwerke Ag | USE OF ELIGIBLE FERRITIC-PERLITIC (AFP) STEELS AS A MATERIAL FOR GAS EXCHANGE VALVES OF COMBUSTION ENGINES |
US5221373A (en) * | 1989-06-09 | 1993-06-22 | Thyssen Edelstahlwerke Ag | Internal combustion engine valve composed of precipitation hardening ferritic-pearlitic steel |
DE4017973A1 (en) * | 1989-06-09 | 1990-12-13 | Thyssen Edelstahlwerke Ag | Precipitation hardenable ferritic pearlitic steel |
DE4109628C2 (en) * | 1990-07-12 | 1997-04-17 | Mahle Gmbh | Use of a precipitation hardening ferritic pearlitic steel |
DE4024381C2 (en) * | 1990-08-01 | 1999-01-28 | Mahle Gmbh | Pistons for internal combustion engines with forged areas made of steel |
US5136992A (en) * | 1990-07-12 | 1992-08-11 | Mahle Gmbh | Piston for internal combustion engines with forged sections made of steel |
DE4137240A1 (en) * | 1991-11-13 | 1993-05-19 | Thyssen Edelstahlwerke Ag | AFP steel used for prodn. of large forged tools - has low sulphur content and uniformly high tensile strength through tempering |
US5282906A (en) * | 1992-01-16 | 1994-02-01 | Inland Steel Company | Steel bar and method for producing same |
ES2128240B1 (en) * | 1996-07-26 | 2000-01-01 | Gsb Grupo Siderurgico Vasco S | PROCEDURE FOR THE MANUFACTURE OF MICROALLOYED STEELS. |
US6083455A (en) * | 1998-01-05 | 2000-07-04 | Sumitomo Metal Industries, Ltd. | Steels, steel products for nitriding, nitrided steel parts |
DE102006007148A1 (en) * | 2006-02-16 | 2007-08-30 | Volkswagen Ag | Piston for internal combustion engines and method for producing a piston for internal combustion engines |
CN100469918C (en) * | 2007-05-28 | 2009-03-18 | 无锡市恒特力金属制品有限公司 | Nb microalloying high strength power metallurgy material and forming method thereof |
JP4609585B2 (en) * | 2008-06-06 | 2011-01-12 | 住友金属工業株式会社 | Soft nitriding steel, soft nitriding steel and crankshaft |
US8241442B2 (en) | 2009-12-14 | 2012-08-14 | Arcelormittal Investigacion Y Desarrollo, S.L. | Method of making a hypereutectoid, head-hardened steel rail |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2023915A1 (en) * | 1968-11-22 | 1970-08-21 | Nippon Kokan Kk | |
FR2087818A5 (en) * | 1970-03-20 | 1971-12-31 | British Steel Corp | |
DE2116357A1 (en) * | 1970-03-26 | 1972-02-03 | Nippon Steel Corp | High strength steel and process for its manufacture |
DE1608162B1 (en) * | 1967-11-13 | 1972-06-29 | Hoesch Ag | USE OF FLAT STEEL PRODUCTS |
FR2274704A1 (en) * | 1974-06-15 | 1976-01-09 | Ferrotest Gmbh | High-tensile steel bars for reinforcing concrete - with optimum formability, weldability and fatigue strength |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5638448A (en) * | 1979-09-03 | 1981-04-13 | Nippon Steel Corp | Nonrefined tough steel |
JPS5716114A (en) * | 1980-07-03 | 1982-01-27 | Daido Steel Co Ltd | Manufacture of steel for hardening by high frequency |
-
1987
- 1987-06-12 DE DE3719569A patent/DE3719569C2/en not_active Expired
- 1987-06-24 EP EP87109046A patent/EP0255597B1/en not_active Expired - Lifetime
- 1987-06-24 ES ES198787109046T patent/ES2027998T3/en not_active Expired - Lifetime
- 1987-06-24 AT AT87109046T patent/ATE70567T1/en not_active IP Right Cessation
- 1987-06-24 DE DE8787109046T patent/DE3775298D1/en not_active Expired - Lifetime
- 1987-07-02 FI FI872933A patent/FI88625B/en not_active Application Discontinuation
- 1987-07-04 KR KR1019870007147A patent/KR880003023A/en not_active Application Discontinuation
- 1987-07-06 US US07/070,047 patent/US4838963A/en not_active Expired - Fee Related
-
1991
- 1991-12-19 GR GR91401970T patent/GR3003399T3/en unknown
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE1608162B1 (en) * | 1967-11-13 | 1972-06-29 | Hoesch Ag | USE OF FLAT STEEL PRODUCTS |
FR2023915A1 (en) * | 1968-11-22 | 1970-08-21 | Nippon Kokan Kk | |
FR2087818A5 (en) * | 1970-03-20 | 1971-12-31 | British Steel Corp | |
DE2116357A1 (en) * | 1970-03-26 | 1972-02-03 | Nippon Steel Corp | High strength steel and process for its manufacture |
FR2274704A1 (en) * | 1974-06-15 | 1976-01-09 | Ferrotest Gmbh | High-tensile steel bars for reinforcing concrete - with optimum formability, weldability and fatigue strength |
Also Published As
Publication number | Publication date |
---|---|
ES2027998T3 (en) | 1992-07-01 |
DE3775298D1 (en) | 1992-01-30 |
EP0255597B1 (en) | 1991-12-18 |
ATE70567T1 (en) | 1992-01-15 |
FI872933A (en) | 1988-01-06 |
FI872933A0 (en) | 1987-07-02 |
US4838963A (en) | 1989-06-13 |
DE3719569C2 (en) | 1988-06-23 |
EP0255597A3 (en) | 1989-01-11 |
FI88625B (en) | 1993-02-26 |
DE3719569A1 (en) | 1988-01-21 |
GR3003399T3 (en) | 1993-02-17 |
KR880003023A (en) | 1988-05-13 |
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