EP0091897B1 - Kaltverfestigender austenitischer Manganhartstahl und Verfahren zur Herstellung desselben - Google Patents

Kaltverfestigender austenitischer Manganhartstahl und Verfahren zur Herstellung desselben Download PDF

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Publication number
EP0091897B1
EP0091897B1 EP83890054A EP83890054A EP0091897B1 EP 0091897 B1 EP0091897 B1 EP 0091897B1 EP 83890054 A EP83890054 A EP 83890054A EP 83890054 A EP83890054 A EP 83890054A EP 0091897 B1 EP0091897 B1 EP 0091897B1
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EP
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Prior art keywords
casting
temperature
manganese steel
weight
content
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.)
Expired
Application number
EP83890054A
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German (de)
English (en)
French (fr)
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EP0091897A1 (de
Inventor
Bernd Dipl.-Ing. Kos
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Voestalpine Stahl GmbH
Original Assignee
Vereinigte Edelstahlwerke AG
Voestalpine Stahl GmbH
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Application filed by Vereinigte Edelstahlwerke AG, Voestalpine Stahl GmbH filed Critical Vereinigte Edelstahlwerke AG
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the invention relates to a strain-hardening austenitic manganese steel with an elongation at break of 10 to 80% and to a method for producing the same.
  • Cold-hardening austenitic manganese steels have a wide range of applications, whereby both castings and forgings as well as rolled material are used.
  • the wide range of applications is particularly given by the high ductility and the good work hardenability.
  • the area of application ranges from castings for hard comminution to bulletproof objects.
  • the valuable properties of the manganese hard stands lie in the combination of the above-mentioned properties of the work hardening ability and its lactility.
  • the work hardening occurs whenever the manganese steel is mechanically, e.g. B. is claimed by impact or shock. Hiebie is likely to convert the austenite in one surface layer into an epsilon martensite.
  • Measurements of work hardening show an increase in hardness from 200 HB to up to 550 HB. There is thus an increase in hardness during use when the casting, forging or the like is subjected to mechanical stress. However, since such objects are also subject to an abrasive stress, this surface layer is continually removed, but a renewed transformation of the austenite now on the surface occurs due to renewed mechanical stress.
  • the alloy located under the surface layer has a high ductility, so that the manganese steels can also withstand high mechanical impact loads without risk of breakage, even with a smaller wall thickness.
  • a casting be it a molded casting or a block casting, is initially manufactured. Due to the properties of this casting, the properties of the objects made from it are then predetermined. If the structure is too coarse in the casting, the ductility of the commodity is then too low. In the case of large castings, as is known per se, this has different grain zones over its cross section. On the outside there is a thin, relatively fine-grained edge zone, which is followed by a zone with coarse stem crystals, which is followed by the center of the casting with a globular structure. Although the steel is essentially austenitic and work hardenable over the entire cross-section, due to the different structure it shows great differences in mechanical properties, in particular in ductility.
  • the casting temperature be as low as possible, e.g. to keep at 1410 ° C, which increases the number of germs with increasing supercooling and a finer grain should be achieved.
  • low casting temperatures lead to great difficulties in production.
  • Cold welding occurs on the casting, furthermore, the rheological properties of the melt are already such that an exact shape, especially in edges, is no longer given.
  • the melt solidifies on the pan lining during casting, which leads to pan shells which then have to be removed and refurbished. During the casting itself, the plug can become stuck in the spout, as a result of which the casting must be stopped.
  • the economic disadvantages which have to be accepted for a non-reproducible grain refinement are so serious that the processes with such a low casting temperature could not prevail.
  • Another method for grain refinement consists of a targeted heat treatment, in which the casting is annealed at a temperature between 500 and 600 ° C. for 8 to 12 hours, whereby a high proportion of the austenite is to be converted to pearlite. Austenitization annealing is then carried out at a temperature between 970 and 1110 ° C. The two-fold change in structure is said to produce a finer grain, but on the equilibrium side the cause is that the product becomes extremely brittle during the heat treatment and breaks even without deformation under less mechanical stress. Another major disadvantage is that this method requires a large amount of energy.
  • Manganese steels usually have a carbon content of 0.7 to 1.7% by weight, with a manganese content of between 5 and 18% by weight to be maintained. essential for the properties of a Manganese steel is also that a ratio of carbon to manganese between 1: 4 and 1:14 is maintained. If the ratio is lower, there is no longer any austenitic steel and it can therefore no longer be work hardened, and at the same time there is less toughness. At a higher ratio, the austenite is too stable, which means that it can no longer be work hardened, so that the desired properties cannot be achieved either.
  • a phosphorus content of more than 0.1% by weight causes an extreme drop in toughness, so that, as is known per se for phosphorus, a particularly low value is aimed for.
  • ASTM A 128/64 describes four different types of high manganese steels, the carbon cold varying between 0.7 and 1.45% by weight and the manganese content between 11 and 14.0% by weight.
  • the carbon content is changed to vary the work hardenability, which is also to be influenced by the addition of chromium.
  • the chromium additives then range between 1.5 and 2.5% by weight.
  • Coarse carbide deposits are to be suppressed by adding up to 2.3% molybdenum.
  • the addition of up to 4.0% by weight of nickel is said to stabilize the austenite, which prevents the formation of pearlite in thick-walled castings.
  • a high manganese steel has already become known which has a manganese content of approximately 5% by weight. With such steels, however, the toughness is already low. However, it has a high wear resistance.
  • the present invention has set itself the goal of creating a strain-hardening austenitic manganese high-carbon steel which has an elongation at break of 10 to 80%, which has a structure that is as uniform as possible over the entire cross section and has a particularly fine grain, at the same time without any deterioration in the mechanical properties should occur.
  • the ratio of carbon to manganese is between 1: 4 and 1:14 has up to 0.05 titanium, 0.05 zirconium and 0.05 vanadium as microalloying elements with the proviso that the sum of titanium and zirconium between 0.002% and 0.05%, optionally also containing vanadium as a microalloying element, the sum of these microalloying elements being up to 0.05% by weight. It was quite surprising that with such a small addition of alloying elements, grain refinement can be achieved while maintaining or increasing the mechanical properties, since additions of 0.1% and above caused the mechanical properties to deteriorate. An exact explanation for this fact has not yet been found. Zircon and vanadium are particularly effective at high casting temperatures.
  • the manganese steel has an additional 0.002 to 0.008% by weight boron, an even smaller grain can be achieved.
  • Grain refinement is particularly good when only 0.01 to 0.025% by weight of titanium is present as the microalloying element.
  • the manganese steel has a content of 0.01 to 0.05% by weight of aluminum, the titanium content can be maintained particularly precisely.
  • an insert being melted in an electric furnace after which calcareous, slag-forming additives are added to the liquid melt and the desired analysis is set and brought to a tapping temperature of 1450 to 1600 ° C. with an oxygen affinity Element is deoxidized and tapped into the ladle, consists essentially in the fact that the content of the microalloying elements titanium, zirconium and vanadium is set in the ladle, and the melt is poured at a temperature between 1420 and 1520 ° C. and again after the casting has cooled heated to austenitizing temperature from 980 to 1150 ° G and then cooled rapidly.
  • microalloying elements By adding the microalloying elements in the ladle, a reproducible content of microalloying elements is achieved. A particularly high level of toughness is achieved by the heat treatment of the casting, heating to an austenitizing temperature of 980 to 1150 ° C. and then rapidly cooling.
  • the susceptibility to cracking in the casting obtained can be significantly reduced.
  • Manganese steel has a lower thermal conductivity than other steels (only one sixth of that of iron), so special attention must be paid to temperature compensation.
  • a reliable dissolution of the grain boundary carbides even with larger cross-sections and with lower energy consumption can be achieved at a temperature between 1080 and 1100 ° C during solution annealing, whereupon the temperature is reduced to 980 to 1000 ° C and equalized and then rapidly cooled becomes.
  • a casting with particularly low internal stresses can be achieved by alternately applying coolants of different thermal conductivity after heating to the austenitizing temperature. Water and air are to be used as particularly suitable coolants.
  • the casting is already removed from the mold at a temperature between 800 and 1000 ° C and then placed in a heat treatment furnace in which the temperature of the casting is equalized, whereupon the temperature is immediately raised to the austenitizing temperature, a particularly energy-saving process is provided, with a build-up of high Tension in the casting is prevented, whereby pearlitization can be avoided.
  • Example 2 The procedure was analogous to Example 1, with titanium in the form of ferrotitanium being added to the ladle.
  • the ladle was brought to the mold and it was poured at 1460 ° C. After the casting had cooled, it was heated to 1100 ° C., at which temperature it was kept for four hours, whereupon the temperature of the furnace was lowered to 1000 ° C. After an hour, a temperature equalization in the casting was reached, followed by cooling with alternating immersion in a water bath.
  • the Turas thus obtained was free from cracks. With the exception of the marginal zone, which was microcrystalline, the metallographic examination revealed a completely uniform, fine-grained structure.
  • the casting had an average titanium content of 0.02% by weight.
  • the mechanical properties were almost identical for the specimens removed in the center and on the edge, the tensile strength being 820 and 830 N / mm 2 and the elongation being 40 and 45%, respectively.
  • Example 2 For the production of a drop-forged hammer with pin for a Gastein mill, which had a weight of 180 kg, a block was cast analogously to Example 2. This block was then cut up, and these parts were drop-forged into impact hammers at a forging temperature of 1050 ° C. These impact hammers had a perfectly fine structure in the area of the pin attachments, which was retained even after solution annealing and quenching. In the case of a hammer which was produced with an alloy according to Example 1, coarse-grained crystals appeared in the area of the pin attachments, which in some cases caused microcracks.
  • Example 2 The procedure was analogous to Example 2, with boron also being added to the ladle in addition to titanium. The temperature trip was observed as in Example 2. The casting had an average titanium content of 0.02% by weight and an average boron content of 0.005% by weight. The micrographs of samples taken at analogous locations showed that there were 50 grains per millimeter in the samples containing only titanium, whereas the samples containing boron had an average of 60 grains, resulting in a decrease in the average grain diameter of 0.02 mm to 0.017 mm.
  • the tensile strength or elongation at break was determined in accordance with DIN 5 D 145/1975.

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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)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Articles (AREA)
EP83890054A 1982-04-13 1983-04-11 Kaltverfestigender austenitischer Manganhartstahl und Verfahren zur Herstellung desselben Expired EP0091897B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT0143582A AT377287B (de) 1982-04-13 1982-04-13 Kaltverfestigender austenitischer manganhartstahl und verfahren zur herstellung desselben
AT1435/82 1982-04-13

Publications (2)

Publication Number Publication Date
EP0091897A1 EP0091897A1 (de) 1983-10-19
EP0091897B1 true EP0091897B1 (de) 1986-11-26

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EP83890054A Expired EP0091897B1 (de) 1982-04-13 1983-04-11 Kaltverfestigender austenitischer Manganhartstahl und Verfahren zur Herstellung desselben

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US (2) US4512804A (enrdf_load_stackoverflow)
EP (1) EP0091897B1 (enrdf_load_stackoverflow)
AT (1) AT377287B (enrdf_load_stackoverflow)
AU (1) AU536111B2 (enrdf_load_stackoverflow)
CA (1) CA1193117A (enrdf_load_stackoverflow)
DE (1) DE3367939D1 (enrdf_load_stackoverflow)
ES (1) ES8405079A1 (enrdf_load_stackoverflow)
IN (1) IN160010B (enrdf_load_stackoverflow)
ZA (1) ZA832425B (enrdf_load_stackoverflow)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009035969A1 (de) * 2009-08-04 2011-02-10 Albert Hoffmann Gmbh Verfahren zum Herstellen eines Antriebsturaskörpers, Antriebsturaskörper Ring und Kettenfahrzeug
DE102023116026A1 (de) * 2023-06-20 2024-12-24 Schaeffler Technologies AG & Co. KG Verfahren zur Herstellung eines Wälzkörpers und danach hergestellter Wälzkörper

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AT390807B (de) * 1983-08-05 1990-07-10 Kos Bernd Austenitischer manganhartstahl und verfahren zu seiner herstellung
AT390806B (de) * 1983-09-23 1990-07-10 Kos Bernd Austenitischer manganhartstahl und verfahren zu seiner herstellung
EP0186512B1 (en) * 1984-12-28 1990-08-08 Nippon Steel Corporation Method for controlling solidification segregation of steel
IN165225B (enrdf_load_stackoverflow) * 1986-03-26 1989-09-02 Bruss Ti Kirova
DE69129157T2 (de) * 1991-12-26 1998-11-05 Mitsui Shipbuilding Eng Legierung mit guten dämpfungseigenschaften
US5575829A (en) * 1995-06-06 1996-11-19 Armco Inc. Direct use of sulfur-bearing nickel concentrate in making Ni alloyed stainless steel
US5865385A (en) * 1997-02-21 1999-02-02 Arnett; Charles R. Comminuting media comprising martensitic/austenitic steel containing retained work-transformable austenite
US6572713B2 (en) 2000-10-19 2003-06-03 The Frog Switch And Manufacturing Company Grain-refined austenitic manganese steel casting having microadditions of vanadium and titanium and method of manufacturing
US20030154110A1 (en) * 2001-11-20 2003-08-14 Ervin Walter Method and apparatus for wireless access to a health care information system
FR2876711B1 (fr) * 2004-10-20 2006-12-08 Usinor Sa Procede de revetement au trempe a chaud dans un bain de zinc des bandes en acier fer-carbone-manganese
ITUD20040228A1 (it) * 2004-12-06 2005-03-06 F A R Fonderie Acciaierie Roia Procedimento per ottenere una lega di acciaio al manganese, e lega di acciaio al manganese cosi' ottenuta
CN100395370C (zh) * 2006-01-05 2008-06-18 同济大学 一种铁路用记忆合金鱼尾螺栓紧固件材料及其制备方法
WO2009046484A1 (en) * 2007-10-08 2009-04-16 Steelfinne Fabrications Pty Ltd Austenitic manganese steel alloy and method for making same
CN102766747B (zh) * 2012-07-09 2013-08-28 山西太钢不锈钢股份有限公司 一种高强无磁耐磨钢的制造方法
US20140261918A1 (en) * 2013-03-15 2014-09-18 Exxonmobil Research And Engineering Company Enhanced wear resistant steel and methods of making the same
CN104480372A (zh) * 2014-12-29 2015-04-01 芜湖金龙模具锻造有限责任公司 一种硼锑合金轧辊材料的制备方法
JP6455333B2 (ja) * 2015-06-23 2019-01-23 新日鐵住金株式会社 高圧水素ガス用高Ｍｎ鋼鋼材ならびにその鋼材からなる、配管、容器、バルブおよび継手
JP6455342B2 (ja) * 2015-06-29 2019-01-23 新日鐵住金株式会社 高圧水素ガス用高Ｍｎ鋼鋼材ならびにその鋼材からなる、配管、容器、バルブおよび継手
US10227681B2 (en) * 2015-10-21 2019-03-12 Caterpillar Inc. High manganese steel with enhanced wear and impact characteristics
CN105369130B (zh) * 2015-10-27 2017-05-03 天津威尔朗科技有限公司 一种多元合金化高强高耐磨钢及热轧板的制造方法
DE102017129819B4 (de) * 2017-12-13 2020-04-23 Craco Gmbh Zerkleinerungsmaschine, Innenraumauskleidung und Verfahren zur Herstellung
US20190376168A1 (en) * 2018-06-12 2019-12-12 Mohsen Askari Paykani High strength alloy steels and methods of making the same
CN109440001B (zh) * 2018-10-31 2020-12-01 西安工程大学 一种含纳米晶奥氏体的多元低合金耐磨铸钢及其制备方法
CN109518077A (zh) * 2018-11-13 2019-03-26 南京钢铁股份有限公司 一种奥氏体和碳化物双相组织的耐磨钢板及其生产方法
WO2022008956A1 (en) * 2020-07-08 2022-01-13 Arcelormittal A method of casting a steel semi-product with high titanium content
WO2024225991A1 (en) * 2023-04-25 2024-10-31 Pinar Döküm Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ A novel composition of hadfield steel and the production method thereof

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102009035969A1 (de) * 2009-08-04 2011-02-10 Albert Hoffmann Gmbh Verfahren zum Herstellen eines Antriebsturaskörpers, Antriebsturaskörper Ring und Kettenfahrzeug
DE102009035969B4 (de) * 2009-08-04 2014-03-06 Albert Hoffmann Gmbh Verfahren zum Herstellen eines Antriebsturaskörpers, Antriebsturaskörper, Ring und Kettenfahrzeug
DE102023116026A1 (de) * 2023-06-20 2024-12-24 Schaeffler Technologies AG & Co. KG Verfahren zur Herstellung eines Wälzkörpers und danach hergestellter Wälzkörper
DE102023116026B4 (de) 2023-06-20 2025-02-13 Schaeffler Technologies AG & Co. KG Verfahren zur Herstellung eines Wälzkörpers und danach hergestellter Wälzkörper

Also Published As

Publication number Publication date
DE3367939D1 (en) 1987-01-15
ZA832425B (en) 1983-12-28
ATA143582A (de) 1984-07-15
AU1316783A (en) 1983-12-01
US4531974A (en) 1985-07-30
IN160010B (enrdf_load_stackoverflow) 1987-06-20
ES521388A0 (es) 1984-05-16
US4512804A (en) 1985-04-23
CA1193117A (en) 1985-09-10
ES8405079A1 (es) 1984-05-16
AT377287B (de) 1985-02-25
AU536111B2 (en) 1984-04-19
EP0091897A1 (de) 1983-10-19

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