EP1420077A1 - Inert material with high hardness for elements used at high temperature - Google Patents
Inert material with high hardness for elements used at high temperature Download PDFInfo
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- EP1420077A1 EP1420077A1 EP02450262A EP02450262A EP1420077A1 EP 1420077 A1 EP1420077 A1 EP 1420077A1 EP 02450262 A EP02450262 A EP 02450262A EP 02450262 A EP02450262 A EP 02450262A EP 1420077 A1 EP1420077 A1 EP 1420077A1
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- alloy
- minus
- hardness
- nitrogen
- manganese
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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
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/34—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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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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- 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
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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
- C22C38/50—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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- 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
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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
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
Definitions
- the invention relates to a material with high inertia, in particular high oxidation resistance and increased hardness for thermally resilient components and tools.
- DIN 50900 is a reaction of a metallic material with its Environment that causes a measurable change in the material as corrosion Are defined. Corrosion can occur with and without mechanical stress on the Component, as well as after various types of chemical attack and different temperatures.
- a surface attack of objects is most common electrochemical corrosion in the presence of an ion conducting phase or through chemical corrosion and hot corrosion at elevated temperatures. Also in molten media at elevated temperature, for example in liquid Glasses can be a corrosive attack with a change in the surface of a metal part in contact therewith.
- Corrosion- and heat-resistant steels and alloys are supposed to, also one thermal resilience with temperatures above 600 ° C because of a cubic face-centered atomic lattice structure or an austenitic structure exhibit. In terms of alloy technology, this means that such materials are higher Have nickel and / or cobalt contents or with a view to an increased Strength and hardness at high temperatures as nickel-based or Cobalt-based alloys are formed, but from corrosion-chemical Cobalt-based alloys are formed, but from corrosion-chemical Chromium content of at least greater than 13 wt .-% must be present.
- the nickel content lower than 36 wt .-% and to increase the corrosion resistance To increase the chromium content of the alloy to over 16% by weight.
- An austenitic iron base material with a nickel content of less than 36 % By weight may be due to a high chromium concentration, possibly in Connection with other corrosion-inhibiting elements, definitely one Corrosion attack at high temperatures, for example at 600 ° C and above, Resist over a required minimum amount of time, however, the material shows a low hardness as well as a similar strength and a limited Creep behavior.
- alloys for example according to DIN material no. 1.2780 and 1.2782 and 1.2786 for reasons of Profitability and for production reasons as tools for one Glass processing used.
- the invention seeks to remedy this and has set itself the goal of being a material Specify initially mentioned type with a hardness of greater than 230 HB, which a high creep resistance even at temperatures above 600 ° C improved durability and similar corrosion resistance having.
- the invention aims to use an iron-based alloy as Material for hot work tools that work at temperatures above 550 ° C be used from.
- a material of the type mentioned at the outset consisting of an alloy with a composition essentially in% by weight of Carbon (C) 0.01 to 0.25 Silicon (Si) 0.35 to 2.5 Manganese (Mn) 0.4 to 4.3 Chrome (Cr) 16.0 to 28.0 Nickel (Ni) 15.0 to 36.0 Nitrogen (N) 0.01 to 0.29 with the proviso that the nickel content of the alloy is equal to or possibly greater by a maximum of 4.8% by weight than the value formed from the content of chromium plus 1.5 silicon minus 0.12 manganese minus 18 nitrogen minus 30 carbon minus the numerical value 6 Ni ⁇ Cr + 1.5 x Si - 0.12 Mn - 18 x N- 30 x C - 6 Rest iron (Fe), as well as accompanying elements and impurities, which material has a hardness of at least 230 HB formed by cold forming.
- the advantages achieved with the invention are in particular the synergy of corrosion-chemical resistance of the selected alloy and that of this chemical composition achievable by means of cold forming Properties of the material.
- cold forming or deformation below the recrystallization temperature of the face-centered cubic austenite the material solidifies by blocking dislocations in the Crystal lattice.
- a related increase in hardness and an increase in The strength of the material according to the invention remains for the person skilled in the art surprisingly, even at temperatures above 600 ° C expected recovery processes in the strained lattice, such as a thermal activated cross sliding and a recombining of dislocations can be done in usual Periods are not observed.
- Impurities can of course degrade the material properties, so that the alloy according to the invention for the accompanying elements and / or impurity elements has concentration values in% by weight of Molybdenum (Mo) less than 1.0 Vanadium (V) to 0.5 Tungsten (W) to 0.5 Copper (Cu) to 0.5 Cobalt (Co) to 6.5 Titanium (Ti) to 0.5 Aluminum (AI) to 1.5 Niobium (Nb) to 0.5 Oxygen (O) max 0.05 Phosphorus (P) max 0.03 Sulfur (S) max 0.03 having.
- the object of the invention is achieved by a method for producing a material for components and tools with high inertia, in particular high oxidation resistance and increased hardness under thermal loads with a temperature of up to 750 ° C, according to which an alloy with a composition in wt.
- Ni 0.5 to 36.0
- the Elasticity limit of the material can be raised to a stress level, which is also close to the work surface of the component or tool at a Volume change due to changing thermal load is not achieved. Accordingly, no zones occur in the area of the grain boundaries, which at Temperature changes are plastically deformed, causing cracking Material fatigue can be avoided. This is also a grain boundary attack largely avoidable by chemical or hot corrosion, so how, for Example with a glass mold, also a high work surface or surface quality with high loads and large quantities of production over a long time preserved.
- Conventional glass shapes on the other hand, often show up after a short time Period of use at the grain boundaries of the structure Have a distance in the range of a few microns. The shaped glass thereby conveying unevenness in the lightwave range, causing reflection interference and frosted glass effects can arise.
- the corrosion and heat resistance can be further increased and a Fatigue cracking can be effectively suppressed if, according to the process the invention by cold working, a material with a hardness greater than 250 HB, especially 300 HB and higher is formed.
- a preliminary product with a composition according to the invention by means of Hot forming formed this is subjected to a solution treatment or from the deformation temperature, if necessary amplified, cooled and is cold formed, a particularly homogeneous material with improved Corrosion resistance can be created.
- the further object of the invention is achieved when using an iron-based alloy with alloying elements in% by weight Carbon (C) up to 0.25 Silicon (Si to 2.5 Manganese (Mn) to 4.3 Chrome (Cr) 16.0 to 28.0 Nickel (Ni) 15.0 to 36.0 Nitrogen (N) 0.01 to 0.29 with the proviso that the nickel content of the alloy is equal to or possibly greater by a maximum of 4.8% by weight than the value formed from the content of chromium plus 1.5 silicon minus 0.12 manganese minus 18 nitrogen minus 30 carbon minus the numerical value 6 Ni ⁇ Cr + 1.5 x Si - 0.12 x Mn - 18 x N - 30 x C - 6 Remainder iron (Fe), as well as accompanying elements and impurities, which alloy is solidified by cold working of the preliminary product formed from it to a material hardness of at least 230 HB, preferably greater than 250 HB, as a material for hot work tools with a working temperature of higher than 555 ° C , preferably
- the strength of the material according to the invention is at Test temperature of 604 ° C depending on the extent of the cold deformation shown.
- the sample material was forged at a temperature of 1010 ° C and increasingly cooled from the forming heat and a solution heat treatment Subject to 1060 ° C. Parts of the material were cold worked with a degree of deformation of 21%, 35%, 47% and 55%, thereafter from it Tensile tests were created. The strength determinations, namely the 0.2% Yield strength and tensile strength took place at a temperature of 604 ° C, where the samples were kept at this temperature for 20 minutes. For comparison standard material was solution annealed at 1060 ° C, producing from it Samples were also examined at 604 ° C.
- the bar chart of Fig. 1 clearly shows an increase in the strength values of the material depending on of the degree of deformation, where (not shown in the diagram) Strength increase to a high degree already with a degree of cold deformation of more than 6%, in particular greater than 12%.
- the fatigue strength of the material according to the invention is at Temperature of 600 ° C, determined by a hardness test in the cold state of the Samples, in comparison with materials according to DIN material No. 1.2083 and material No. 1.4028.
- the comparison materials No. 1.2083 and No. 1.4028 were hardened in oil from 1020 ° C, tempered at 630 ° C and also the Long-term annealing exposed. After 45, 90, 140 and 180 hours, that became Sample material taken out of the oven, allowed to cool and the material hardness checked, after which a reinsertion of the samples (with a Thermal shock).
- the comparative material H 5 showed a expected behavior of hardness, whereas that with 35% cold-formed Material H 525 according to the invention has an increased hardness of 315 HB and a high hardness Exhibited endurance behavior. At 600 ° C even with changing thermal No reduction in hardness and no creeping of the material determined become. In contrast, the martensitic standard steels were used significant drop in hardness was observed with the glow duration of the samples.
Abstract
Description
Die Erfindung betrifft einen Werkstoff mit hoher Reaktionsträgheit, insbesondere hoher Oxidationsbeständigkeit und erhöhter Härte für thermisch belastbare Bauteile und Werkzeuge.The invention relates to a material with high inertia, in particular high oxidation resistance and increased hardness for thermally resilient components and tools.
Nach DIN 50900 ist eine Reaktion eines metallischen Werkstoffes mit seiner Umgebung, die eine meßbare Veränderung des Werkstoffes bewirkt, als Korrosion definiert. Eine Korrosion kann dabei mit und ohne mechanische Belastung des Bauteiles, sowie nach verschiedenen Arten eines chemischen Angriffes und bei unterschiedlichen Temperaturen erfolgen.According to DIN 50900 is a reaction of a metallic material with its Environment that causes a measurable change in the material as corrosion Are defined. Corrosion can occur with and without mechanical stress on the Component, as well as after various types of chemical attack and different temperatures.
Am häufigsten wird ein Oberflächenangriff von Gegenständen durch eine elektrochemische Korrosion in Gegenwart einer ionenleitenden Phase oder durch chemische Korrosion und Heißkorrosion bei erhöhten Temperaturen bewirkt. Auch in schmelzflüssigen Medien bei erhöhter Temperatur, zum Beispiel in flüssigen Gläsern, kann ein Korrosionsangriff mit einer Veränderung der Oberfläche eines damit in Berührung stehenden Metallteiles erfolgen.A surface attack of objects is most common electrochemical corrosion in the presence of an ion conducting phase or through chemical corrosion and hot corrosion at elevated temperatures. Also in molten media at elevated temperature, for example in liquid Glasses can be a corrosive attack with a change in the surface of a metal part in contact therewith.
In der modernen Technik sind Bau- und Werkzeugteile zumeist einer Mehrzahl von verschiedenen Beanspruchungen gleichzeitig ausgesetzt, von denen insbesondere die thermischen und mechanischen Belastungen auch wechselnd oder schwellend wirksam sein können. Dementsprechend liegen vielfach intensivierte Korrosionsbedingungen vor, welche gegebenenfalls durch eine Verformung der oberflächennahen Zone des Teiles verstärkt werden.In modern technology, components and tool parts are mostly a number of exposed to different stresses at the same time, in particular the thermal and mechanical loads also alternating or swelling can be effective. Accordingly, there are many intensified Corrosion conditions, which may be caused by a deformation of the near the surface of the part.
Korrosions- und hitzebeständige Stähle und Legierungen sollen, auch einer thermischen Belastbarkeit mit Temperaturen über 600°C wegen, einen kubisch flächenzentrierten Atomgitteraufbau bzw. eine austenitische Gefügestruktur aufweisen. Legierungstechnisch bedeutet dies, dass derartige Werkstoffe höhere Nickel- und/oder Kobaltgehalte aufweisen oder im Hinblick auf eine gesteigerte Festigkeit und Härte bei hohen Temperaturen als Nickelbasis- oder Kobaltbasislegierungen ausgebildet sind, wobei jedoch aus korrosionschemischen Kobaltbasislegierungen ausgebildet sind, wobei jedoch aus korrosionschemischen Gründen ein Chromgehalt von zumindest größer als 13 Gew.-% vorliegen muss.Corrosion- and heat-resistant steels and alloys are supposed to, also one thermal resilience with temperatures above 600 ° C because of a cubic face-centered atomic lattice structure or an austenitic structure exhibit. In terms of alloy technology, this means that such materials are higher Have nickel and / or cobalt contents or with a view to an increased Strength and hardness at high temperatures as nickel-based or Cobalt-based alloys are formed, but from corrosion-chemical Cobalt-based alloys are formed, but from corrosion-chemical Chromium content of at least greater than 13 wt .-% must be present.
Obwohl ein Werkstoff mit einer hohen Nickelkonzentration durchwegs erhöhte mechanische Festigkeit bzw. hohe Materialhärte aufweist, wodurch die Gebrauchseigenschaften von Bau- und Werkzeugteilen bei hoher Temperatur verbessert sind, besteht aus wirtschaftlichen Gründen der Wunsch, den Nickelgehalt unter 36 Gew.-% zu senken und zur Steigerung der Korrosionsbeständigkeit den Chromanteil der Legierung auf über 16 Gew.-% anzuheben.Although a material with a high nickel concentration consistently increased has mechanical strength or high material hardness, whereby the Usage properties of components and tool parts at high temperature are improved, there is a desire for economic reasons, the nickel content lower than 36 wt .-% and to increase the corrosion resistance To increase the chromium content of the alloy to over 16% by weight.
Ein austenitischer Eisenbasiswerkstoff mit einem Nickelgehalt von weniger als 36 Gew.-% kann zwar auf Grund einer hohen Chromkonzentration, gegebenenfalls in Verbindung mit weiteren korrosionshemmenden Elementen, durchaus einem Korrosionsangriff bei hohen Temperaturen, beispielsweise bei 600°C und darüber, über eine geforderte Mindestzeitdauer widerstehen, allerdings weist der Werkstoff eine geringe Härte sowie eine dergleichen Festigkeit und ein eingeschränktes Zeitstandsverhalten auf. Trotz dieser Nachteile werden beispielsweise Legierungen gemäß DIN Werkstoff Nr. 1.2780 und 1.2782 und 1.2786 aus Gründen der Wirtschaftlichkeit und aus Erstellungsgründen als Werkzeuge für eine Glasverarbeitung eingesetzt.An austenitic iron base material with a nickel content of less than 36 % By weight may be due to a high chromium concentration, possibly in Connection with other corrosion-inhibiting elements, definitely one Corrosion attack at high temperatures, for example at 600 ° C and above, Resist over a required minimum amount of time, however, the material shows a low hardness as well as a similar strength and a limited Creep behavior. Despite these disadvantages, alloys, for example according to DIN material no. 1.2780 and 1.2782 and 1.2786 for reasons of Profitability and for production reasons as tools for one Glass processing used.
Hier will die Erfindung Abhilfe schaffen und setzt sich zum Ziel, einen Werkstoff der eingangs genannten Art mit einer Härte von größer als 230 HB anzugeben, welcher auch bei Temperaturen über 600°C einen hohen Kriechwiderstand und ein verbessertes Dauerstandsverhalten sowie eine dergleichen Korrosionsfestigkeit aufweist.Here, the invention seeks to remedy this and has set itself the goal of being a material Specify initially mentioned type with a hardness of greater than 230 HB, which a high creep resistance even at temperatures above 600 ° C improved durability and similar corrosion resistance having.
Weiters ist es Aufgabe der Erfindung, ein Verfahren zur wirtschaftlichen Herstellung eines Werkstoffes für Bauteile und Werkzeuge zu schaffen, welche verbesserte Gebrauchseigenschaften bei hoher Härte und erhöhter Korrosionsbeständigkeit besitzen.Furthermore, it is an object of the invention to provide a process for economical production to create a material for components and tools that improved Performance characteristics with high hardness and increased corrosion resistance have.
Schließlich zielt die Erfindung auf die Verwendung einer Eisenbasislegierung als Werkstoff für Warmarbeitswerkzeuge, die bei Arbeitstemperaturen von über 550°C eingesetzt werden, ab.Finally, the invention aims to use an iron-based alloy as Material for hot work tools that work at temperatures above 550 ° C be used from.
Das vorher genannte Ziel wird bei einem Werkstoff der eingangs genannten Art,
bestehend aus einer Legierung mit einer Zusammensetzung im wesentlichen in
Gew.-% von
Die mit der Erfindung erzielten Vorteile liegen insbesondere in der Synergie von korrosionschemischem Widerstand der ausgewählten Legierung und den bei dieser chemischen Zusammensetzung mittels einer Kaltumformung erreichbaren Eigenschaften des Werkstoffes. Bei einer Kaltumformung bzw. bei einer Verformung unterhalb der Rekristallisationstemperatur des kubisch flächenzentrierten Austenits erfolgt eine Verfestigung des Werkstoffes durch ein Blockieren von Versetzungen im Kristallgitter. Eine damit verbundene Härtesteigerung und eine Erhöhung der Festigkeit des erfindungsgemäßen Werkstoffes bleibt, für den Fachmann überraschend, auch bei Verwendungstemperaturen von über 600°C erhalten, die erwarteten Erholvorgänge im verspannten Gitter, wie zum Beispiel ein thermisch aktiviertes Quergleiten und ein Rekombinieren von Versetzungen können in üblichen Zeiträumen nicht beobachtet werden. Mit anderen Worten: Eine durch eine Kaltverformung erhöhte Warmfestigkeit des erfindungsgemäß zusammengesetzten Werkstoffes bleibt entgegen der Fachmeinung auch bei hohen Verwendungstemperaturen des Bauteiles erhalten, weil ein hoher Kriechwiderstand des Stahles dessen Dauerstandsverhalten verbessert. Gerade bei schwellender thermischer Belastung, wie dies bei einer Kokille für die Herstellung von Gebrauchsgläsern der Fall ist, treten an der Arbeitsoberfläche jeweils starke Temperaturschwankungen und somit örtliche Volumsänderungen des Werkstoffes auf. Es wurde gefunden, dass durch eine erfindungsgemäß erhöhte Materialhärte und Warmfestigkeit die örtliche bzw. oberflächennahe Verformung des Werkstoffes, zum Beispiel einer Glaskokille, in dessen elastischem Bereich erfolgt und dass dadurch einer Ermüdungsrißbildung, die bei auch geringen plastischen Formänderungen eintritt und zum Ausfall der Form führen kann, entgegengewirkt wird.The advantages achieved with the invention are in particular the synergy of corrosion-chemical resistance of the selected alloy and that of this chemical composition achievable by means of cold forming Properties of the material. In the case of cold forming or deformation below the recrystallization temperature of the face-centered cubic austenite the material solidifies by blocking dislocations in the Crystal lattice. A related increase in hardness and an increase in The strength of the material according to the invention remains for the person skilled in the art surprisingly, even at temperatures above 600 ° C expected recovery processes in the strained lattice, such as a thermal activated cross sliding and a recombining of dislocations can be done in usual Periods are not observed. In other words, one by one Cold forming increased the heat resistance of the composite according to the invention Contrary to the specialist opinion, material remains high Preserve usage temperatures of the component because of a high creep resistance of the steel improves its creep behavior. Especially with swelling thermal stress, as is the case with a mold for the production of Glasses are the case, strong on the work surface Temperature fluctuations and thus local volume changes in the material on. It was found that material hardness increased according to the invention and heat resistance the local or near-surface deformation of the material, for example, a glass mold, in the elastic range and that this leads to fatigue crack formation, even with low plastic Form changes occur and can lead to failure of the form, counteracted becomes.
Um ein verbessertes Eigenschaftsprofil des Werkstoffes sicherzustellen, ist es wichtig, dass dieser auch bei einer Kaltverformung im stabil austenitischen Bereich bleibt und keine Zonen mit Verformungsmartensit aufweist. Dies wird erfindungsgemäß durch die in Grenzen angegebene Nickel- und Chromkonzentration und durch den einschränkend vorgegebenen Konzentrationsbereich von Nickel in Abhängigkeit von Chrom, Silizium, Mangan, Stickstoff und Kohlenstoff erreicht. Höhere Nickelgehalte verschlechtern, wie sich gezeigt hat, das Dauerstandsverhalten. Hingegen wird bei niedrigen Nickelkonzentrationen die Austenitstabilität und die Warmfestigkeit des Werkstoffes sprunghaft verringert. Im wesentlichen gilt Gleiches für die Elemente Kohlenstoff und Stickstoff, wobei insbesondere Stickstoff die Dauerstandsfestigkeit des Werkstoffes erhöht.To ensure an improved property profile of the material, it is It is important that this also applies to cold forming in the stable austenitic range remains and has no zones with deformation martensite. this will according to the invention by the nickel and Chromium concentration and given by the restrictive Concentration range of nickel depending on chromium, silicon, manganese, Nitrogen and carbon reached. Higher nickel levels deteriorate as has shown the creep behavior. In contrast, at low Nickel concentrations, the austenite stability and the heat resistance of the material abruptly reduced. Essentially the same applies to the elements carbon and nitrogen, nitrogen in particular being the fatigue strength of the Material increased.
Die Gebrauchseigenschaften von erfindungsgemäßen Bauteilen und Werkzeugen
können verbessert werden, wenn der Werkstoff für ein oder mehrere
Legierungselemente Gehalte in Gew.-% von
Obwohl die Elemente Molybdän, Vanadin, Wolfram, Titan und Niob den Kriechwiderstand des Materials bei hohen Temperaturen erhöhen und Kupfer, sowie Aluminium, klassische Aushärtungselemente darstellen, weisen diese Stahlbegleiter im Werkstoff nach der Erfindung eine höchst zuverlässige Konzentration auf, weil, wie gefunden wurde, höhere Gehalte derselben den Korrosionswiderstand insbesondere bei zeitweiser Berührung mit teigigem Glas, erniedrigen und auf Grund einer gebildeten Oberflächenrauhigkeit der Form die Glastransparenz verschlechtern. Die Ursache dafür ist noch nicht ausreichend geklärt, jedoch zählen die Akzeptoratome Na+, K+, Ca2+ , B 3+, Al3+ und Si 4+ zu den harten Lewis-Säuren, wobei nach jeder Glasformung eine Heißkorrosionsbelastung der Form gegeben ist.Although the elements molybdenum, vanadium, tungsten, titanium and niobium increase the creep resistance of the material at high temperatures and copper, as well as aluminum, are classic hardening elements, these steel companions have a highly reliable concentration in the material according to the invention because, as was found, higher contents of the same reduce the corrosion resistance, in particular if they come into contact with pasty glass at times, and, due to the surface roughness of the mold, impair the transparency of the glass. The reason for this has not yet been sufficiently clarified, but the acceptor atoms Na + , K + , Ca 2+ , B 3+ , Al 3+ and Si 4+ are hard Lewis acids, with the mold exposed to hot corrosion after each glass molding is.
Verunreinigungen können naturgemäß die Werkstoffeigenschaften verschlechtern,
so dass die erfindungsgemäße Legierung für die Begleitelemente und/oder
Verunreinigungselemente Konzentrationswerte in Gew.-% von
Die Aufgabe der Erfindung wird durch ein Verfahren zur Herstellung eines
Werkstoffes für Bauteile und Werkzeuge mit hoher Reaktionsträgheit, insbesondere
hoher Oxidationsbeständigkeit und erhöhter Härte bei thermischen Belastungen mit
einer Temperatur von bis zu 750°C, nach welchem aus einer Legierung mit einer
Zusammensetzung in Gew.-% von im wesentlichen
Mittels einer Kaltverformung der erfindungsgemäßen Legierung kann die Elastizitätsgrenze des Werkstoffes auf ein Spannungsniveau angehoben werden, welches auch nahe der Arbeitsfläche des Bauteiles oder Werkzeuges bei einer Volumsänderung durch wechselnde thermische Belastung nicht erreicht wird. Dementsprechend treten auch im Bereich der Korngrenzen keine Zonen, die beim Temperaturwechsel plastisch verformt werden, auf, wodurch eine Rißbildung durch Materialermüdung vermieden werden kann. Damit ist auch ein Korngrenzenangriff durch chemische oder Heißkorrosion weitgehend vermeidbar, so dass, wie zum Beispiel bei einer Glasform, eine hohe Arbeitsflächen- bzw. Oberflächengüte auch bei hohen Belastungen und bei großen Stückzahlen der Fertigung über lange Zeit erhalten bleibt. Herkömmliche Glasformen hingegen zeigen oft nach kurzer Einsatzdauer an den Korngrenzen des Gefüges Materialabtragungen, welche einen Abstand im Bereich von wenigen µm aufweisen. Dem geformten Glas werden dadurch Unebenheiten im Lichtwellenbereich vermittelt, wodurch Reflexions-Interferenzen und Milchglaseffekte entstehen können.By means of cold working the alloy according to the invention, the Elasticity limit of the material can be raised to a stress level, which is also close to the work surface of the component or tool at a Volume change due to changing thermal load is not achieved. Accordingly, no zones occur in the area of the grain boundaries, which at Temperature changes are plastically deformed, causing cracking Material fatigue can be avoided. This is also a grain boundary attack largely avoidable by chemical or hot corrosion, so how, for Example with a glass mold, also a high work surface or surface quality with high loads and large quantities of production over a long time preserved. Conventional glass shapes, on the other hand, often show up after a short time Period of use at the grain boundaries of the structure Have a distance in the range of a few microns. The shaped glass thereby conveying unevenness in the lightwave range, causing reflection interference and frosted glass effects can arise.
Die Korrosions- und die Warmfestigkeit können weiter erhöht und eine Ermüdungsrißbildung wirksam unterdrückt werden, wenn, verfahrensgemäß nach der Erfindung durch Kaltverformung, ein Werkstoff mit einer Härte von größer als 250 HB, insbesondere von 300 HB und höher gebildet wird.The corrosion and heat resistance can be further increased and a Fatigue cracking can be effectively suppressed if, according to the process the invention by cold working, a material with a hardness greater than 250 HB, especially 300 HB and higher is formed.
Wenn ein Vorprodukt mit einer erfindungsgemäßen Zusammensetzung mittels Warmverformung gebildet, dieses einer Lösungsglühbehandlung unterworfen oder von der Verformungstemperatur, gegebenenfalls verstärkt, abgekühlt und kaltverformt wird, kann ein besonders gefügehomogener Werkstoff mit verbesserter Korrosionsfestigkeit erstellt werden.If a preliminary product with a composition according to the invention by means of Hot forming formed, this is subjected to a solution treatment or from the deformation temperature, if necessary amplified, cooled and is cold formed, a particularly homogeneous material with improved Corrosion resistance can be created.
Insbesondere für weitgehend achssymmetrisch ausgeformte Werkzeuge, wie Flaschenkokillen und dergleichen, kann es von Vorteil sein, wenn die Kaltverformung des Materials vollumfänglich radial senkrecht zur Längsachse des Vorproduktes durchgeführt wird.Especially for largely axially symmetrical tools, such as Bottle molds and the like, it can be beneficial if the Cold deformation of the material completely radially perpendicular to the longitudinal axis of the Intermediate product is carried out.
Für eine gesteigerte Güte des Erzeugnisses ist vorgesehen, dass die Legierung mit
Gehalten von einem oder mehreren Legierungselementen in Gew.-%
Schließlich wird das weitere Ziel der Erfindung bei einer Verwendung einer
Eisenbasislegierung mit Legierungselementen in Gew.-% von
Besonders vorteilhaft, hinsichtlich der Produktgüte und einer wirtschaftlichen Herstellung, ist eine Verwendung der vorgenannten Eisenbasislegierung als Werkzeugwerkstoff in der Glasindustrie, insbesondere als Formenwerkstoff für Maschinenpreßgläser.Particularly advantageous in terms of product quality and economical Manufacturing, is a use of the aforementioned iron base alloy as Tool material in the glass industry, especially as a mold material for Maschinenpreßgläser.
Anhand von vergleichenden Untersuchungsergebnissen soll der erfindungsgemäße Werkstoff näher dargestellt werden.Based on comparative test results, the invention Material are shown in more detail.
Es zeigen
In Fig. 1 ist die Festigkeit des erfindungsgemäßen Werkstoffes bei einer Prüftemperatur von 604°C in Abhängigkeit vom Ausmaß der Kaltverformung dargestellt. Das Probematerial wurde bei einer Temperatur von 1010°C geschmiedet und aus der Umformhitze verstärkt abgekühlt und einer Lösungsglühbehandlung bei 1060°C unterworfen. An Teilen des Materials erfolgte jeweils eine Kaltverformung mit einem Umformgrad von 21 %, 35 %, 47 % und 55 %, wonach daraus Zugproben erstellt wurden. Die Festigkeitsermittlungen, und zwar die 0,2 % Dehngrenze und die Zugfestigkeit, erfolgten bei einer Temperatur von 604°C, wobei die Proben 20 Minuten auf dieser Temperatur gehalten wurden. Zum Vergleich wurde Standardmaterial bei 1060°C lösungsgeglüht, wobei daraus gefertigte Proben ebenfalls bei 604°C untersucht wurden. Das Balkendiagramm von Fig. 1 zeigt deutlich eine Erhöhung der Festigkeitswerte des Werkstoffes in Abhängigkeit vom Verformungsgrad, wobei (im Diagramm nicht dargestellt) eine Festigkeitssteigerung in hohem Ausmaß schon bei einem Kaltverformungsgrad von mehr als 6 %, insbesondere von größer als 12 %, gegeben ist.In Fig. 1, the strength of the material according to the invention is at Test temperature of 604 ° C depending on the extent of the cold deformation shown. The sample material was forged at a temperature of 1010 ° C and increasingly cooled from the forming heat and a solution heat treatment Subject to 1060 ° C. Parts of the material were cold worked with a degree of deformation of 21%, 35%, 47% and 55%, thereafter from it Tensile tests were created. The strength determinations, namely the 0.2% Yield strength and tensile strength took place at a temperature of 604 ° C, where the samples were kept at this temperature for 20 minutes. For comparison standard material was solution annealed at 1060 ° C, producing from it Samples were also examined at 604 ° C. The bar chart of Fig. 1 clearly shows an increase in the strength values of the material depending on of the degree of deformation, where (not shown in the diagram) Strength increase to a high degree already with a degree of cold deformation of more than 6%, in particular greater than 12%.
In Fig. 2 ist die Dauerstandsfestigkeit des erfindungsgemäßen Werkstoffes bei einer Temperatur von 600°C, ermittelt durch eine Härteprüfung im kalten Zustand der Proben, im Vergleich mit Materialien nach DIN Werkstoff Nr. 1.2083 und Werkstoff Nr. 1.4028 dargestellt.2, the fatigue strength of the material according to the invention is at Temperature of 600 ° C, determined by a hardness test in the cold state of the Samples, in comparison with materials according to DIN material No. 1.2083 and material No. 1.4028.
Der erfindungsgemäße Werkstoff wurde mit einer Zusammensetzung von in Gew.-% C = 0,08, Si = 1,7, Mn = 1,15, P = 0,01, S = 0,002, Cr = 24,8, Ni = 19,8, N = 0,02, Mo = 0,26, V = 0,09, W = 0,11, Cu = 0,12, Co = 0,4, Ti = 0,01, Al = 0,02, Nb = 0,001, O = 0,0029 erschmolzen, zu einem Versuchsblock gegossen und dieser zu Probenmaterial warmverformt. Am Probenmaterial erfolgte eine Lösungsglühbehandlung bei 1060°C mit einem anschließenden Abschrecken im Wasser, wonach Proben mit der Bezeichnung H 5 unverformt und Proben mit der Bezeichnung H 525 mit einer Kaltverformung von 35 % einer Langzeitglühung bei 600°C unterworfen wurden. Die Vergleichswerkstoffe Nr. 1.2083 und Nr. 1.4028 wurden von 1020°C in Öl gehärtet, bei 630°C angelassen und ebenfalls der Langzeitglühung ausgesetzt. Nach 45, 90, 140 und 180 Stunden wurde das Probenmaterial aus dem Ofen genommen, erkalten gelassen und die Materialhärte geprüft, wonach ein Rückeinsetzen der Proben ( mit einer Temperaturwechselbelastung) erfolgte. Das Vergleichsmaterial H 5 zeigte ein erwartetes Verhalten der Härte, wogegen der mit 35 % kaltverformte erfindungsgemäße Werkstoff H 525 eine erhöhte Härte von 315 HB und ein hohen Dauerstandsverhalten aufwies. Bei 600°C konnte auch bei wechselnder thermischer Belastung keine Härteminderung und kein Kriechen des Materiales festgestellt werden. Im Gegensatz dazu wurde an den martensitischen Normstählen ein deutlicher Härteabfall mit der Glühdauer der Proben festgestellt.The material according to the invention has a composition of in Wt% C = 0.08, Si = 1.7, Mn = 1.15, P = 0.01, S = 0.002, Cr = 24.8, Ni = 19.8, N = 0.02, Mo = 0.26, V = 0.09, W = 0.11, Cu = 0.12, Co = 0.4, Ti = 0.01, Al = 0.02, Nb = 0.001, O = 0.0029 melted, poured into a test block and closed Sample material thermoformed. A was carried out on the sample material Solution heat treatment at 1060 ° C with subsequent quenching in the Water, after which samples with the designation H 5 undeformed and samples with the Designation H 525 with a cold deformation of 35% in long-term annealing 600 ° C were subjected. The comparison materials No. 1.2083 and No. 1.4028 were hardened in oil from 1020 ° C, tempered at 630 ° C and also the Long-term annealing exposed. After 45, 90, 140 and 180 hours, that became Sample material taken out of the oven, allowed to cool and the material hardness checked, after which a reinsertion of the samples (with a Thermal shock). The comparative material H 5 showed a expected behavior of hardness, whereas that with 35% cold-formed Material H 525 according to the invention has an increased hardness of 315 HB and a high hardness Exhibited endurance behavior. At 600 ° C even with changing thermal No reduction in hardness and no creeping of the material determined become. In contrast, the martensitic standard steels were used significant drop in hardness was observed with the glow duration of the samples.
Claims (13)
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SI200230449T SI1420077T1 (en) | 2002-01-23 | 2002-11-15 | Inert material with high hardness for elements used at high temperature |
AT02450262T ATE341651T1 (en) | 2002-01-23 | 2002-11-15 | REACTION CARRIER MATERIAL WITH INCREASED HARDNESS FOR THERMALLY STRESSED COMPONENTS |
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AT0010702A AT410550B (en) | 2002-01-23 | 2002-01-23 | Material used as a tool material in the glass industry, especially as a molding material for machine pressed glass consists of an alloy containing carbon, silicon, chromium, nickel and nitrogen |
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EP1420077A1 true EP1420077A1 (en) | 2004-05-19 |
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US (1) | US20030136482A1 (en) |
EP (1) | EP1420077B1 (en) |
KR (1) | KR100540851B1 (en) |
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DK (1) | DK1420077T3 (en) |
ES (1) | ES2273992T3 (en) |
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TW (1) | TWI225102B (en) |
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EP2246454A1 (en) * | 2008-02-27 | 2010-11-03 | Sumitomo Metal Industries, Ltd. | Carburization-resistant metal material |
CN102650023A (en) * | 2011-02-23 | 2012-08-29 | 宝山钢铁股份有限公司 | Cu-Fe-Ni-Cr austenite alloy for oil bushing |
WO2018160515A1 (en) * | 2017-03-03 | 2018-09-07 | Borgwarner Inc. | Nickel and chrome based iron alloy having enhanced high temperature oxidation resistance |
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EP1605072B1 (en) * | 2003-03-20 | 2012-09-12 | Sumitomo Metal Industries, Ltd. | Stainless steel for high pressure hydrogen gas, vessel and equipment comprising the steel |
US20090053100A1 (en) * | 2005-12-07 | 2009-02-26 | Pankiw Roman I | Cast heat-resistant austenitic steel with improved temperature creep properties and balanced alloying element additions and methodology for development of the same |
UA100460C2 (en) * | 2008-11-19 | 2012-12-25 | Сандвік Інтеллекчуал Проперті Аб | Nickel based alloy capable for forming ALUMINA |
EP2224031B1 (en) | 2009-02-17 | 2013-04-03 | MEC Holding GmbH | Wear resistant alloy |
EP2287351A1 (en) | 2009-07-22 | 2011-02-23 | Arcelormittal Investigación y Desarrollo SL | Heat-resistant austenitic steel having high resistance to stress relaxation cracking |
CN101921967A (en) * | 2010-08-12 | 2010-12-22 | 江苏新华合金电器有限公司 | Novel austenitic heat-resistance stainless steel |
US9347121B2 (en) * | 2011-12-20 | 2016-05-24 | Ati Properties, Inc. | High strength, corrosion resistant austenitic alloys |
PL3590643T3 (en) * | 2018-07-02 | 2021-07-05 | Höganäs Ab (Publ) | Wear-resistant iron-based alloy compositions comprising nickel |
CN110724873A (en) * | 2018-07-17 | 2020-01-24 | 宝钢特钢有限公司 | High-wear-resistance die forging die steel and manufacturing method thereof |
RU2703318C1 (en) * | 2019-04-15 | 2019-10-16 | Акционерное Общество "Российский Концерн По Производству Электрической И Тепловой Энергии На Атомных Станциях" (Ао "Концерн Росэнергоатом") | Radiation-resistant austenitic steel for the wwpr in-vessel partition |
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Also Published As
Publication number | Publication date |
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EP1420077B1 (en) | 2006-10-04 |
HK1067668A1 (en) | 2005-04-15 |
KR20030064304A (en) | 2003-07-31 |
DE50208351D1 (en) | 2006-11-16 |
ES2273992T3 (en) | 2007-05-16 |
TWI225102B (en) | 2004-12-11 |
CA2416950C (en) | 2007-08-28 |
CN1434146A (en) | 2003-08-06 |
KR100540851B1 (en) | 2006-01-10 |
US20030136482A1 (en) | 2003-07-24 |
RU2246553C2 (en) | 2005-02-20 |
CA2416950A1 (en) | 2003-07-23 |
DK1420077T3 (en) | 2007-02-05 |
RU2003101774A (en) | 2005-01-10 |
BR0300116A (en) | 2003-09-09 |
ATA1072002A (en) | 2002-10-15 |
AT410550B (en) | 2003-05-26 |
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