Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C37/00—Cast-iron alloys
  • C22C37/04—Cast-iron alloys containing spheroidal graphite
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C33/00—Making ferrous alloys
  • C22C33/08—Making cast-iron alloys
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
  • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
  • F16D65/00—Parts or details
  • F16D65/02—Braking members; Mounting thereof
  • F16D65/12—Discs; Drums for disc brakes
  • F16D65/125—Discs; Drums for disc brakes characterised by the material used for the disc body
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
  • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
  • F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
  • F16D69/02—Composition of linings ; Methods of manufacturing
  • F16D69/027—Compositions based on metals or inorganic oxides

Definitions

• the present invention relates to iron alloys and processes for their production. Iron alloys in accordance with the invention are particularly suitable for use in disc brakes for vehicles and in other vehicular, especially automatic components.
• Disc brakes were introduced into motor cars in the late 1950's.
• Disc brakes comprise a disc or rotor that is rigidly connected to the vehicle wheel hub.
• Two or more pads close by caliper action onto the disc or rotor in order to stop rotation of the disc or rotor and hence brake the vehicle.
• the pads have a friction lining which used to be composed of an asbestos material.
• the asbestos material served to substantially protect the pads from heat and mineral attack.
• brake pads are now generally composed of a friction material which contains 10-20% volume resins, 0-10% volume friction modifiers, 0-10% volume metal powders, 20-40% volume fillers and 10-50% volume fibers (asbestos, metal, fibreglass and synthetic mineral fibres).
• gray cast iron Since the introduction of disc brakes, gray cast iron has been the material of choice for manufacture of the discs or rotors. Compared with nodular cast iron, gray cast iron has greater thermal conductivity, a lower modulus of elasticity and is dimensionally stable above 500°C. Nodular cast irons have been considered to be unsuitable for use in disc brakes because they exhibit a too low thermal resistance. Although gray cast iron has many properties that make it especially suitable for use in disc brakes, it does have the drawback of relatively low tensile strength. A number of authors have tried to address this drawback.
• the patent proposed a chromium-nickel cast iron having a composition of 3.20- 3.55% carbon, 0.15-0.25% chromium, 1.15 to 1.35% nickel, 0.30 to 0.50% molybdenum, 0.50 to 0.80% manganese, 1.80 to 2.00% silicon, less than 0.10% phosphorus, less than 0.08% sulphur, balance iron.
• the alloy had a microstructure comprising uniform fine-grained pearlite in which a minimum of 75% type A plate graphite is evenly distributed.
• Japanese Patent Application No. 60-52553 in the name of Sumitomo Kinzoku Kogyo K.K. discloses a steel for a disc brake rotor having 0.1-0.6% carbon, less than 0.8% silicon, less than 3% manganese, 0.2-5.0% nickel and optionally containing one or more of 0.5-5.0% aluminium, 0.1-3.0% copper, 0.2- 3.0% titanium and 0.1-5.0% Mo.
• This steel is described as having a braking resistance equivalent to that of cast iron without spoiling the excellent resistance to thermal cracking of the forged steel rotor.
• United States Patent No. 5,323,883 in the name of Mibe et. al. (assigned to Nissan Motor Company, Limited) relates to an automotive brake system.
• the brake system includes a rotor made of graphitic cast iron consisting of 3.5-4.0% carbon, 1.6-2.0% silicon, 0.5-0.8% manganese, 0.4-1.2% molybdenum, the remainder essentially iron.
• the matrix structure of the composition is in the form of a pearlite.
• This patent emphasises the importance of obtaining good thermal conductivity in materials used for disc brakes.
• the patent also states that if more than 1.2% Mo is added, carbides or casting defects can be created, thereby setting the upper level of molybdenum at 1.2%.
• Manganese is also an essential component of the metal alloy.
• United States Patent No. 1,762,109 in the name of Taylor et. al. discloses a cast iron alloy which may be easily hardened and which may be more readily machined than ordinary cast iron.
• the cast iron alloy consists of 1.0-4.0% carbon, 0.5-2.5% silicon, 1.0-4.0% nickel and up to 1.0% molybdenum, balance iron and incidental impurities.
• the alloy is useful for manufacturing articles in which some portions have a hardened surface and other portions are relatively soft for machining and other purposes, such as tappets, cylinder blocks and pistons.
• United States Patent No. 3,095,300 in the name of Moore et. al. discloses a cast iron composition that includes 1.2-5.3% manganese and 0.40-0.80% molybdenum and that provides a cast iron that is machineable as-cast and which can be hardened in air.
• United States Patent No. 3,798,027 to Defranco et. al. discloses a high strength, low hardness gray cast iron that consists of 1-3% aluminium, 2-4% carbon, up to 1% silicon and the balance iron, the alloy also having been inoculated with an inoculant selected from calcium, strontium and barium.
• This patent suggests that in order to obtain certain particular properties, such as heat resistance or corrosion resistance, various quantities of alloying elements must be added, including, 0-6% copper, 0-12% nickel, 0-5% chromium, 0-2% molybdenum, and 0-1% zirconium.
• United States Patent No. 4,166,756 to Geyes et. al. relates to the metallurgy of wear resistant damping elements used in railroad car trucks.
• this patent relates to the chemical composition and process control parameters, such as pouring temperature, dumping from the mould temperature and cooling rate in order to develop the desired microstructure in the castings.
• the alloy used has a chemical composition consisting of 3.00-3.30% carbon, 1.20-1.50% silicon, 0.85- 1.00% manganese, 0.80-0.90% Molybdenum, 1.40-1.60% (nickel plus copper), balance iron.
• the process for forming castings from that chemistry is described as critical.
• United States Patent No. 4,450,019 to Satou et. al. describes a ductile cast iron which exhibits high resistance to oxidation at high temperatures and thermal fatigue when used as a material for automobile exhaust manifolds.
• the cast iron consists of 2.5-3.8% carbon, 3.5-4.8% silicon, 1.0% or less manganese, 0.1% or less phosphorus, 0.1% as less sulphur, 0.5-2.0% molybdenum, 0.03-0.1% magnesium, at least one of cerium and lanthanum in an amount of 0.02-0.5%, balance iron. If silicon is present in an amount of less than 3.5%, a protective layer of SiO 2 cannot form on the exhaust manifold and casting defects, such as shrinkage cavities, tend to result due to the degree of saturation of carbon.
• Cerium and lanthanum are essential elements of the composition. If Ce and La are present at less than the lower limit of 0.02%, silicon will not disperse towards the surface region of the casting (which is required to form the protective SiO 2 layer on the casting) and the property of Mo inhibiting the resistance to oxidation satisfactorily. Thus, Ce and La must be present in order to counteract the deleterious properties of the molybdenum present in the alloy.
• tappets for internal combustion engines were made from an iron alloy consisting of 3.10-3.60% carbon, 2.00-2.90% silicon, 0.60-0.90% manganese, 0.20-0.80% chromium, 0.30 to 0.60% nickel, 1.50 to 5.00% molybdenum, 0.10-0.50%) vanadium, balance iron.
• Molybdenum was chosen as the main alloy element for several reasons, one of which was that molybdenum forms two types of carbide: a face-centred cubic M 23 C 6 iron-molybdenum carbide and an orthorhombic Fe 3 C cementite carbide. The M 23 C 6 type carbide is more stable.
• the chromium and vanadium are added to the alloy in order to dissolve the cementite type carbides, showing the criticality of adding Cr and V.
• MMC metal matrix composites
• United States Patent No. 5,261,511 in the name of Libsch describes a brake rotor made from a composition having from 20-80 vol% silicon carbides and 80-20 vol% of an iron alloy.
• the patent states that the iron alloy consists essentially of 0.4-4.0% carbon (by weight), 1.8-18.0% silicon, 1.0-10.0% X, where X is selected from a group consisting of Cr, Mo, Cu, Mn, Ni, P and S, balance iron.
• X is present in an amount of 1.51% by weight and is made up of Cr (0.13), Mo (0.08), Cu (0.28), Mn(0.75), Ni (0.13), P (0.06) and S (0.08).
• the patent also states that the metal matrix composite, which incorporates 20-80% of silicon carbide particles and 80-20% of the iron alloy, is an effective material for manufacturing brake rotors. No mention at all is made of the suitability of the iron alloy by itself as a material for manufacture of the brake rotor and the patent specifically requires the presence of silicon carbide particles.
• United States Patent No. 3,909,252 to Kuriyama et. al. describes a wear resistant and self lubricating cast iron.
• the cast iron consists of 1.0-3.5% carbon, 0.5-3.5% silicon, 0.1-1.5% manganese, 0.1-2.0% chromium, 1.0-15.0% cobalt, 0.5-10.0% molybdenum, 0.1-5.0% nickel, 0.05-2.0% niobium, 0.001-0.1% boron, balance iron.
• This cast iron, which contains a large amount of cobalt and additions of chromium and niobium, is especially suitable for manufacturing piston rings.
• United States Patent No. 3,559,775 in the name of Miller describes a brake rotor made from a hypereutectic gray cast iron composition consisting of 3.6-4.0% carbon, 2.5-4.0%) silicon and up to about 2% of one or more pearlite stabilising elements, and iron.
• the pearlite stabilising elements may be manganese, chromium, copper, tin and molybdenum.
• the patent states that the specified pearlite stabilising elements may be used alone or in combination, the only example that included molybdenum as a pearlite stabiliser utilised 0.10- 0.20%) molybdenum, and the molybdenum was used in combination with chromium.
• the chemically uncombined carbon was present in the form of relatively large discrete bodies of graphite of ASTM type A (i.e. flakes of graphite).
• the present invention provides an iron alloy that is particularly suitable for use in manufacturing disc brake rotors, and can also be used in manufacturing a wide variety of other automotive components and other articles.
• the present invention provides an iron alloy containing from 1.5-4.5% by weight carbon, from 1.5 to 4.5% by weight silicon and from at least 0.1% to 6.5% by weight molybdenum, optionally nickel and copper and wherein (molybdenum + nickel + copper) does not exceed 6.5% by weight, balance iron and incidental impurities.
• the amount of carbon preferably falls within the range of from 1.5 to 3.8, more preferably 3.0 to 3.5%, more preferably from 3.0 to 3.35%, most preferably about 3.25%.
• the amount of silicon in the iron alloy preferably falls within the range of from 1.9 to 2.5%, and more preferably from 2.1 to 2.3%.
• Molybdenum is an essential component of the alloy and is present in an amount of at least 1.0%. Molybdenum is preferably present in an amount of at least 1.0% to 4.5%, more preferably at least 1.0% to 3.0%>, even more preferably 1.1 to 3.0%), most preferably 1.2% to 3.0%. It has been found that an alloy containing 1.5% molybdenum is suitable for use in the disc brake rotors of passenger cars whilst disc brakes rotors for racing cars advantageously contain 3.0% molybdenum.
• the iron alloy is a spheroidal graphite cast iron.
• Nickel and/or copper may also be present and function as alloy modifiers to improve the strength and refine the structure of the alloy.
• nickel is present in an amount of 0.1 to 4.5%, more preferably 0.1 to 3.5% and most preferably 1%.
• the amount of copper is preferably 0.1 to 4.5%, more preferably 0.1 to 3.5% and most preferably 1%.
• the total amount of molybdenum and nickel and/or copper should not exceed 6.5%.
• the incidental impurities may include manganese, sulphur and phosphorus.
• the amount of impurities is generally in the range of 0.1 to 0.8%, preferably 0.04% sulphur and 0.04% phosphorus.
• a particularly preferred alloy of the present invention contains 3 to 3.35% carbon, 1.9 to 2.5% silicon and at least 1 to 3% molybdenum, the balance being iron and incidental impurities.
• a preferred composition of the alloy includes 3.5 to 4.5% carbon, 2.1 to 2.3% silicon, 2.5 to 3.5% molybdenum, balance iron and incidental impurities, more preferably 3.7-3.8% carbon, about 3.0% molybdenum, 2.1-2.3% silicon, balance iron and incidental impurities.
• Nickel and/or copper may optionally be included in the amounts specified above.
• the carbon equivalent (CE) of this particularly preferred alloy is generally 3.8.
• nickel and/or copper may optionally be included in the alloy of the present invention in the amounts indicated above without substantial deleterious effects being observed, in one embodiment it is preferred that deliberate additions of nickel and copper to the alloy be minimised or avoided altogether. It is especially preferred that the iron alloy of the present invention have nickel and/or copper present in impurity amounts only.
• chromium, manganese, vanadium, and rare earth metals should be present in the iron alloy of the present invention at substantially zero levels, and certainly no higher than impurity levels. Chromium and manganese act to increase the hardness of the alloy, thereby making it difficult to machine. Further alloying elements would also undesirably increase the cost of making the alloy and could have unknown or undesirable effects on the microstructure and/or the physical properties of the alloy.
• the iron alloy will also contain small amounts of one or more spheroidizing agents.
• Spheroidizing agents typically include some magnesium and accordingly the iron alloy may include small amounts of magnesium.
• the iron alloy may contain small amounts of elements used in other spheroidizing agents known to be suitable to the man skilled in the art.
• the spheroidizing agent is preferably present in a maximum amount of 0.1% to 0.2%.
• the most preferred iron alloy of the present invention comprises 3 to 3.35% carbon, 2.1-2.3%) silicon, at least 1.0 to 3% molybdenum, balance iron and incidental impurities, in which the iron alloy is a spheroidal graphite cast iron.
• Molybdenum is the main alloying element added to the iron alloy of the present invention. It has been found that molybdenum has a stabilising effect on the alloy in that it acts to suppress phase transitions in the alloy as temperature changes occur. When used in the manufacture of disc brake rotors, braking causes the rotors to heat up and cool down. The stabilising effect of the molybdenum minimises or avoid phase transitions which thereby assist in maintaining dimensional stability of the rotors and minimises or avoids cracking of the rotor. It is believed that molybdenum also increases the thermal conductivity of the alloy to thereby assist in improving heat dissipation from the rotors. Molybdenum also refines the grain to produce an alloy having a fine grain size.
• the present inventor has conducted extensive searching of prior art literature and has not located any document that discloses an iron alloy having the composition specified herein.
• Another distinguishing feature of the present invention lies in providing the specified composition in the form of a spheroidal graphite cast iron.
• the iron alloy of the present invention is especially suitable for use in manufacturing disc brake rotors for vehicles, such as automobile, airplanes and trains.
• the present invention provides a disc brake rotor, characterised in that it is composed wholly or partly of the iron alloy of the first aspect of the present invention.
• the iron alloy of the present invention is used in the manufacture of disc brake rotors, it has been found that the disc rotors exhibit reduced wear. Shudder, cracking and squealing, when compared with conventional disc brakes manufactured from gray cast iron, is also reduced.
• iron alloy of the present invention is especially suitable for manufacturing disc brake rotors
• other articles may be made from the iron alloy of the present invention.
• other articles that may be made from the iron alloy of the present invention include vehicle, aircraft or ship parts including, keels, cylinder heads, cylinder blocks and wheels; ash and dust systems, pulverised fuel lines, wear plates for air control or burner boxes, particularly for use in power stations; pump bodies and covers; pipework; crusher parts; gear wheels and pinions; wear plates; dust feeding valves; water supply valves; couplings and other pipe connectors; cast flights; manhole covers and frames; grates; rollers; camshafts; crankshafts; knuckle joints on suspension systems; flywheels; and clutch plates; truck brake rotors; and brake drums for vehicles.
• an iron alloy as described herein comprising the steps of: a) providing a melt including iron, silicon, carbon, molybdenum and optionally copper and/or nickel; and b) casting the melt.
• step (a) includes the step of melting cast iron, ferro silicon alloy, recarburiser and ferro molybdenum alloy.
• An inoculant may also be added to the melt.
• the melt is also preferably treated with a spheroidizing agent to cause any chemically uncombined carbon to be present in the cooled alloy in the form of spheres or nodules, rather than flakes.
• the melting step (a) may be performed in any suitable apparatus such as a furnace, for example, an induction furnace.
• the ingredients melted are preferably well mixed so that the alloy elements are distributed throughout.
• the temperature of the furnace is preferably above about 1350°C.
• the melt in the furnace is then advantageously tapped into a preheated ladle.
• the iron alloy may be cast iron, spheroidal graphite (SG) iron or structural steel.
• the iron alloy is, for example, BHP-300PLUS which contains 0.22% C, 0.50% Si, 1.6% Mn 0.040% P, 0.040% S and a CE of 0.45.
• the ferro silicon alloy contains 70 to 75% Si and 1.5 to 2% Al, the balance being iron and incidental impurities.
• the recarburiser serves to increase the amount of carbon present in the alloy and may be a crushed electrode material, for example, Carbonin 101 which contains 98.0% carbon, 1.0% moisture, 0.5% volatile matter, 1.0% ash, 0.07% sulphur and 0.02% nitrogen.
• the ferro molybdenum alloy contains 67% Mo, 1% Si, 0.6% S and 0.04% P, the balance being iron and incidental impurities.
• the melt may be optionally subjected to a metal treatment such as spheroidizing which converts flakes into spheres.
• a metal treatment such as spheroidizing which converts flakes into spheres.
• This can be achieved by adding a magnesium ferro silicon alloy which suitably contains 6.3% Mg, 46.6% Si, 0.82% Al, 1.09% Ca and 0.99% Re, the balance being iron and incidental impurities.
• Other spheroidizing agents known to the person of skill in the art may also be used, including nickel magnesium ferro silicon spheroidizing agents.
• the inoculant of step (b) refines the grains of the alloy and is preferably ZL80 which contains 71% Si, 1.6% Al, 1.89% Zr and 0.83% Ca, the balance being iron and incidental impurities.
• a nodularity modifier such as Spheroflux may then be added to the melt if desired.
• the casting step preferably occurs before fade takes place otherwise the castings may be inferior. It is generally preferred that casting occur up to 10 minutes after addition of the innoculant, more preferably about 7 minutes. Castings are advantageously allowed to cool in the moulds, preferably overnight.
• Figure 1 is a graph showing the results of an inertial dynamometer disc brake wear test for a disc rotor made from an iron alloy in accordance with the present invention
• Figure 2 is a graph showing the results of an inertial dynamometer disc brake wear test for an original equipment (OE) disc rotor
• Figures 3 and 4 show the results of low pressure wear tests using rotors made in accordance with the present invention and OE rotors;
• Figure 5 shows a photomicrograph of the cast edge of an etched test bar in accordance with the present invention at magnification xlOO;
• Figure 6 shows a photomicrograph at magnification xlOO of a mid-radius section of the test bar in accordance with the present invention;
• Figure 7 shows a photomicrograph of the general area of the test bar shown in Figure 6, but at magnification x500.
• Figure 8 is a photomicrograph similar to Figure 7 but at a magnification of x200.
• the ingredients were melted in the furnace at 1400°C.
• the melt was then treated with 7 kg of a magnesium ferro silicon alloy which acts as a spheroidizing agent, 1.2 kg of an innoculant ZL80 and 0.8 kg of Spheroflux which is a nodularity modifier.
• the melt was stirred thoroughly so as to ensure adequate distribution of the alloy. Casting of the melt in a teapot ladle occurred within 7 minutes so as to ensure that there was no fade.
• the castings were then poured into moulds and allowed to cool overnight.
• the resultant iron alloy had the following composition: 3.25% carbon; 2.1% silicon; 1.5% molybdenum; and 93.15% iron and incidental impurities.
• the resultant iron alloy had the following composition: 3.25% carbon;
• DTV dynamometer test which equates to 20,000km of normal vehicle usage; full inertia dynamometer test, which simulate wear in normal driving conditions; damping test, which measures disc rotor noise; and cracking test, which involves bench testing at various simulated speeds at different standard rates.
• Tables 1 and 2 below give the raw data obtained from the inertia dynamometer disc brake wear test for rotors made from the iron alloy in accordance with the present invention (Table 1) and for original equipment (OE) disc rotors (Table 2). These results are shown graphically in Figures 1 and 2. TABLE 1
• the total wear determined by this test for rotors made from the alloy of the present invention was 0.069mm, whereas the original equipment (OE) rotors showed total wear of 0.102 mm.
• Figures 3 and 4 shows the results of the low pressure wear test using rotors made in accordance with the present invention (referred to in Figures 3 and 4 as "Camcast rotor") and OE rotors.
• Camcast rotor rotors made in accordance with the present invention
• Figures 3 and 4 show some anamolous results, particularly with regard to wear appearing to decrease at increased loads. These tests are being run again but the results are not yet available.
• the data in Figures 3 and 4 that can be reliably interpreted shows that disc rotors in accordance with the present invention display superior wear properties to the OE rotors.
• DTV disc thickness variation
• disc rotors in accordance with the invention have superior performance to OE disc rotors. Indeed, it is believed that disc rotors in accordance with the present invention will provide the following benefits, when compared with OE disc rotors: Eliminates shudder; Will not crack;
• test sample having a composition in accordance with the present invention
• the test sample was in the form of a test bar of 30mm diameter and having the following composition: Carbon 3.7%
• Figure 5 shows a photomicrograph taken at magnification xlOO of the cast edge of the test bar.
• the test bar was etched in 2% nital solution.
• Figure 5 shows a typical nodular cast iron structure showing well defined spheroidal graphite (particularly in the surface to sub-surface regions) in a matrix that consists of ferrite and pearlite and a complex carbide formed during initial solidification. It is postulated that as the melt cools from liquid, graphite forms nodules which then act as nuclei around which ferrite grows. As the ferrite grows, the remaining liquid (rich in carbon and alloying ingredients, especially molybdenum) goes into the interstitial space. This liquid contains the complex carbide and it forms an austenite phase having the complex carbide associated therewith. The austenite is then transformed into pearlite as the casting further cools.
• the complex carbides are thought to be formed from the liquid and hence they are fairly uniformly distributed.
• Figure 6 shows a photomicrograph at magnification xlOO of the test bar etched in 2% nital solution. This shows a microstructure showing the presence of the spheroidal graphite (predominantly in "degraded” or less spherical morphologies) together with the ferrite, pearlite and complex carbide constituents. The pearlite is present and approximately 20% (by area fraction) of the microstructure.
• Figure 7 shows a photomicrograph at magnification x500, etched in 2% nital solution, of the same general region of the test bar as shown in Figure 6.
• Figure 8 is similar to Figure 7, but magnification was x200. Details of the microstructure have been labelled in Figure 7.
• Microhardness testing of the phases was also conducted using lOOg Hv (vickers hardness) and are also reported below: A - degraded graphite nodule (form IV) B - ferrite surrounding the graphite nodules, microhardness using Hv lOOgm is typically 200 C - pearlite occupying the previously interdendritic regions, microhardness is typically 400
• D - complex carbide believed to be of the type M 6 C, where M would be variable combinations of Fe, Mo and other carbide-forming elements.
• the complex carbide is present as a skeleton-like compound in the previously interdendritic regions and representing approximately 5% (by area fraction) of the microstructure. Microhardness measurements of the "skeletons" (including the carbide plus pearlite) is typically 550 plus.
• test bar showed degraded spheroidal graphite towards the centre of the bar. However, the test bar was still clearly classified as a spheroidal graphite cast iron. The degradation near the centre was possibly caused by slower cooling in that region due to the relatively large diameter (30mm) of the test bar. It is expected that articles of thinner section, such as disc brake rotors that are typically of thickness 10- 12mm, would not suffer from spheroidal graphite degradation or that the degradation would be minimised.
• the presence of the complex carbide phase in the alloy of the present invention was unexpected and the testing officer commented that he had never before seen such a phase in a cast iron.
• the alloy had a microstructure comprising very soft nodules of graphite surrounded by relatively soft and ductile ferrite. These soft parts are strengthened and hardened by the pearlite phase and the very hard complex carbide phase.
• the preliminary micrographic analysis conducted to date did not locate any bainite.
• the microstructure discussed above can be obtained from the as-cast condition.

Landscapes

• Engineering & Computer Science (AREA)
• Chemical & Material Sciences (AREA)
• Mechanical Engineering (AREA)
• General Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Inorganic Chemistry (AREA)
• Braking Arrangements (AREA)
• Contacts (AREA)
• Powder Metallurgy (AREA)

Priority Applications (10)

Applications Claiming Priority (2)

Related Child Applications (2)

Publications (1)

Family

ID=3804062

Family Applications (1)

Country Status (12)

Cited By (13)

Families Citing this family (26)

Citations (4)

Family Cites Families (7)

• 1997
  • 1997-10-14 AU AUPO9782A patent/AUPO978297A0/en not_active Abandoned
• 1998
  • 1998-10-14 PL PL98339902A patent/PL339902A1/xx unknown
  • 1998-10-14 NZ NZ504014A patent/NZ504014A/xx unknown
  • 1998-10-14 RU RU2000112018/02A patent/RU2216604C2/ru not_active IP Right Cessation
  • 1998-10-14 AT AT98951096T patent/ATE331820T1/de not_active IP Right Cessation
  • 1998-10-14 EP EP98951096A patent/EP1029098B1/en not_active Expired - Lifetime
  • 1998-10-14 KR KR1020007004035A patent/KR100565862B1/ko not_active Expired - Fee Related
  • 1998-10-14 DE DE69835099T patent/DE69835099T2/de not_active Expired - Lifetime
  • 1998-10-14 CA CA002305902A patent/CA2305902C/en not_active Expired - Fee Related
  • 1998-10-14 JP JP2000516073A patent/JP2001520313A/ja active Pending
  • 1998-10-14 WO PCT/AU1998/000858 patent/WO1999019525A1/en not_active Ceased
  • 1998-10-14 BR BR9814608-4A patent/BR9814608A/pt not_active IP Right Cessation

Patent Citations (4)

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events