CA2190953A1 - Iron-chromium-boron alloy for glass manufacturing tools - Google Patents
Iron-chromium-boron alloy for glass manufacturing toolsInfo
- Publication number
- CA2190953A1 CA2190953A1 CA002190953A CA2190953A CA2190953A1 CA 2190953 A1 CA2190953 A1 CA 2190953A1 CA 002190953 A CA002190953 A CA 002190953A CA 2190953 A CA2190953 A CA 2190953A CA 2190953 A1 CA2190953 A1 CA 2190953A1
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- Canada
- Prior art keywords
- tool according
- alloy
- tool
- chromium
- carbon
- 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.)
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B9/00—Blowing glass; Production of hollow glass articles
- C03B9/30—Details of blowing glass; Use of materials for the moulds
- C03B9/48—Use of materials for the moulds
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Articles (AREA)
- Powder Metallurgy (AREA)
Abstract
An iron-chromium-boron alloy, suitable for the production of tools for the manufacture of glass articles, and a tool made from the alloy, has a composition of from I to 20 wt.% chromium and from 0.5 to 3 wt.% boron. The composition optionally contains carbon subject to carbon in excess of 1.0 wt.% being bound by at least one strong carbide forming element in a carbide and/or carbo-boride phase, with the alloy otherwise optionally including the at lest one carbide forming element. The composition also optionally contains one or more of silicon up to 3 wt.%, aluminium up to 0.2 wt.%,mananese up to 2 wt.%, nickel up to 3 wt.%, copper up to 3 wt.% and melybdenum up to 5 wt.%. The balance, apart from incidental impurities,is iron.
Description
IRoN-cHRoMluM-BoRoN ALLOY FOR GLASS MANUFACTURING TOOLS
This invention is concern~d with improved tooling used in the manufacture of glass articles, such as glass containers, and with an alloy for such tooling.Glass containers are made by forming molten glass, at temperatures above the glass softening temperature. The glass may be made from either recycled glass or from a mixture of raw materials that includes lime, soda ash, silica sand and other additives. During the forming operation, an amount of molten glass at a temperature over 1200C is placed into a metal die and shaped by blowing air through a metal nozle. In most manufacturing operations the shaping process is repeated at high rates and significant wear is experienced by tools such as the metal "blow nozle" or plunger which is in contact with what becomes the neck of the glass container and through which the air is blown.
In glass shaping machinery the metal components or tools such as nozles and other tools, that come into contact with the hot glass, must have high hardness and high wear resistance as well as high resistance to oxidation and scaling. Because of the rapid thermal cycling that occurs through repeated contact with molten glass and removal of the glass from the die, metal components or tools should have a high resistance to thermal cracking. In most types of glass container manufacture, the metal tooling experiences many thousands of thermal cycles before being re-machined or replaced.
In conventional tooling used in the manufacture of glass bottles, the "blow-blow plunger" forms the inside of the neck of the bottie, as well as enabling air to be blown to press the molten glass against the wall of the die. Such blow-blow plungers and other glass moulding components are conventionally made from nickel boron alloys containing 2 to 3 wt% boron, usually 98 ~t% nickel and 2 wt%boron. These alloys produce a microstructure of nickel dendrites and a eutectic mixture of nickel and nickel boride. This material has a good thermal shock resistance and a reasonable hardness of about 40 to 45 Rockwell C. However, the nickel matrix is relatively soft and cannot be hardened by heat treatment. The 3û soft matrix contributes to two problems:
(a) the matrix wears relatively rapidly compared to ~he eutectic borides and thetotal wear resistance is lowered by this mechanism: and " ~ 21 90953 WO 95133080 PCTtAU95/00312
This invention is concern~d with improved tooling used in the manufacture of glass articles, such as glass containers, and with an alloy for such tooling.Glass containers are made by forming molten glass, at temperatures above the glass softening temperature. The glass may be made from either recycled glass or from a mixture of raw materials that includes lime, soda ash, silica sand and other additives. During the forming operation, an amount of molten glass at a temperature over 1200C is placed into a metal die and shaped by blowing air through a metal nozle. In most manufacturing operations the shaping process is repeated at high rates and significant wear is experienced by tools such as the metal "blow nozle" or plunger which is in contact with what becomes the neck of the glass container and through which the air is blown.
In glass shaping machinery the metal components or tools such as nozles and other tools, that come into contact with the hot glass, must have high hardness and high wear resistance as well as high resistance to oxidation and scaling. Because of the rapid thermal cycling that occurs through repeated contact with molten glass and removal of the glass from the die, metal components or tools should have a high resistance to thermal cracking. In most types of glass container manufacture, the metal tooling experiences many thousands of thermal cycles before being re-machined or replaced.
In conventional tooling used in the manufacture of glass bottles, the "blow-blow plunger" forms the inside of the neck of the bottie, as well as enabling air to be blown to press the molten glass against the wall of the die. Such blow-blow plungers and other glass moulding components are conventionally made from nickel boron alloys containing 2 to 3 wt% boron, usually 98 ~t% nickel and 2 wt%boron. These alloys produce a microstructure of nickel dendrites and a eutectic mixture of nickel and nickel boride. This material has a good thermal shock resistance and a reasonable hardness of about 40 to 45 Rockwell C. However, the nickel matrix is relatively soft and cannot be hardened by heat treatment. The 3û soft matrix contributes to two problems:
(a) the matrix wears relatively rapidly compared to ~he eutectic borides and thetotal wear resistance is lowered by this mechanism: and " ~ 21 90953 WO 95133080 PCTtAU95/00312
- 2 -(b) wear of the nickel matrix often results in m,croscopic wear particles becoming imbedded in the inside of the glass container.
In most glass bottle manufacturing operations, wear is a major problem; the wear of blow-blow plungers, for example, necessitate their removal after between5 7 and 14 days of continuous operation in order for it to be re-machined. Also,particles which become embedded in the glass of containers results in a reduction of the shatter strength of a typical bottle by a factor of 4 to 5. Several defective bottles in a batch can result in wholesale rejection of a run due to the possibility of failure in the hands of a consumer with possible legal or recall consequences.
Resistance to thermal shock, combined with resistance to wear caused by repeated contact with molten glass, is of paramount importance for materials used for tools such as blow-blow plungers and push-blow plungers that are used in the manufacture of glass containers.
The present invention is directed to providing improved ferrous alloys suitable for manufacture of tools, which have high resistance to both wear and thermal shock, for the manufacture of glass articles such as containers. The invention also provides such tools cast from such alloys.
A tool according to the invention may comprise a blow nozle or plunger, such as a blow-blow plunger or a push-blow plunger. However, the tool may comprise any other component of machinery for use in the manufacture of glass articies, such as containers, which component is used in forming the article by contact with molten glass. The component thus may comprise a die or die section used for shaping a glass article.
An alloy according to the invention is an iron-chromium-boron alloy. The 2~ alloy has from 1 to 20 wt% chromium, from 0.~ to 3 wt% boron, up to 1.0 wt%
carbon or higher if substantial amounts of strong carbide forming elements such as molybdenum, vanadium, titanium, niobium and tungsten are present, optional alloying additions as detailed in the following, and a balance apart from incidental impurities of iron.
A tool according to the invention is cast from a melt of the alloy of the invention, and can achieve a high hardness and resistance to wear, coupled with a high resistance to thermal shock. The tool also has a high resistance to Wo ')~/33080 PCI'/AU95/00312
In most glass bottle manufacturing operations, wear is a major problem; the wear of blow-blow plungers, for example, necessitate their removal after between5 7 and 14 days of continuous operation in order for it to be re-machined. Also,particles which become embedded in the glass of containers results in a reduction of the shatter strength of a typical bottle by a factor of 4 to 5. Several defective bottles in a batch can result in wholesale rejection of a run due to the possibility of failure in the hands of a consumer with possible legal or recall consequences.
Resistance to thermal shock, combined with resistance to wear caused by repeated contact with molten glass, is of paramount importance for materials used for tools such as blow-blow plungers and push-blow plungers that are used in the manufacture of glass containers.
The present invention is directed to providing improved ferrous alloys suitable for manufacture of tools, which have high resistance to both wear and thermal shock, for the manufacture of glass articles such as containers. The invention also provides such tools cast from such alloys.
A tool according to the invention may comprise a blow nozle or plunger, such as a blow-blow plunger or a push-blow plunger. However, the tool may comprise any other component of machinery for use in the manufacture of glass articies, such as containers, which component is used in forming the article by contact with molten glass. The component thus may comprise a die or die section used for shaping a glass article.
An alloy according to the invention is an iron-chromium-boron alloy. The 2~ alloy has from 1 to 20 wt% chromium, from 0.~ to 3 wt% boron, up to 1.0 wt%
carbon or higher if substantial amounts of strong carbide forming elements such as molybdenum, vanadium, titanium, niobium and tungsten are present, optional alloying additions as detailed in the following, and a balance apart from incidental impurities of iron.
A tool according to the invention is cast from a melt of the alloy of the invention, and can achieve a high hardness and resistance to wear, coupled with a high resistance to thermal shock. The tool also has a high resistance to Wo ')~/33080 PCI'/AU95/00312
- 3 -oxidation.
The alloy and the tool of the invention have the further benefit of being able to be softened by annealing and re-hardened to high hardness levels. Also, particularly with alloys with a high chromium content, such as at least 8 wt%, they 5 have a high chromium content matrix which can be hardened to martensite with heat treatment and is hard and corrosion resistant. This matrix, coupled with the presence of hard iron-chromium eutectic borides, provides a material with much better wear resistance under conditions of elevated temperatures and rapid thermal cycling or heat shock.
The iron-chromium-boron alloy and tools cast therefrom withstand wear for much longer periods than the nickel-boron alloy discussed above, and with their excellent oxidation resistance, the tools produce bottles which do not suffer from alloy metal contamination and thus give a more reliable product.
The iron-chromium-boron alloy and tools cast therefrom can be softened to 1~ 35 Rockwell C by annealing, enabling machining, then re-hardening by heating to above 900C and air cooling. Tempering can then further adjust hardness if needed.
The alloy and the tool also can be provided with a high level of surface finish, achievable by polishing.
The iron-chromium-boron alloy and tool according to the invention can be substantially free of carbon, with carbon present effectively only as an incidental impurity. However, as indicated, carbon can be present at up to 1.0 wt%.
Preferably carbon does not exceed 0.6 wt%, and may for example be present at from 0.1 to 0.6 wt%, such as from 0.1 to 0.3 wt%. The boron content is not less 2~ than 0.5 ~t%, and most preferably is from 0.5 to 2.5 wt%, such as from 1 to2.5 wt%. For most applications, the preferred chromium content is from 3 to 18 wt%, such as from 8 to 18 wt%.
If strong carbide forming elements, such as mclybdenum, vanadium, titanium, tungsten and niobium, are included in the alloy composition then the 3~ carbon level may be in excess of 1.0 wt% provided that the level of strong carbide forming elements is such that the excess carbon is bound by these elements in carbide or carbo-boride phases. The carbon content of the matrix would then -WO ')5/33080 PCT/Ali~100312
The alloy and the tool of the invention have the further benefit of being able to be softened by annealing and re-hardened to high hardness levels. Also, particularly with alloys with a high chromium content, such as at least 8 wt%, they 5 have a high chromium content matrix which can be hardened to martensite with heat treatment and is hard and corrosion resistant. This matrix, coupled with the presence of hard iron-chromium eutectic borides, provides a material with much better wear resistance under conditions of elevated temperatures and rapid thermal cycling or heat shock.
The iron-chromium-boron alloy and tools cast therefrom withstand wear for much longer periods than the nickel-boron alloy discussed above, and with their excellent oxidation resistance, the tools produce bottles which do not suffer from alloy metal contamination and thus give a more reliable product.
The iron-chromium-boron alloy and tools cast therefrom can be softened to 1~ 35 Rockwell C by annealing, enabling machining, then re-hardening by heating to above 900C and air cooling. Tempering can then further adjust hardness if needed.
The alloy and the tool also can be provided with a high level of surface finish, achievable by polishing.
The iron-chromium-boron alloy and tool according to the invention can be substantially free of carbon, with carbon present effectively only as an incidental impurity. However, as indicated, carbon can be present at up to 1.0 wt%.
Preferably carbon does not exceed 0.6 wt%, and may for example be present at from 0.1 to 0.6 wt%, such as from 0.1 to 0.3 wt%. The boron content is not less 2~ than 0.5 ~t%, and most preferably is from 0.5 to 2.5 wt%, such as from 1 to2.5 wt%. For most applications, the preferred chromium content is from 3 to 18 wt%, such as from 8 to 18 wt%.
If strong carbide forming elements, such as mclybdenum, vanadium, titanium, tungsten and niobium, are included in the alloy composition then the 3~ carbon level may be in excess of 1.0 wt% provided that the level of strong carbide forming elements is such that the excess carbon is bound by these elements in carbide or carbo-boride phases. The carbon content of the matrix would then -WO ')5/33080 PCT/Ali~100312
- 4 -remain low.
The fracture toughness, therrnal shock resistance and wear resistance of the cast ferrous alloys is largely determined by the volume fraction of hard phases, which in turn is a function of the content of both boron and carbon and carbide and boride forming elements, and also the interstitial boron and carbon content of the matrix. The boron content of the matrix is always low because thesolubility of boron in ferrite and austenite is low. tiowever the solubility of carbon in austenite and therefore the carbon content of the martensitic matrix can be as high as approximately 2 wt% unless the carbon is bound in some other phase.
It is overriding in the design of satisfactory alloy compositions for the present invention that the carbon content of the matrix is kept to a low enough level for sufficient fracture toughness or thermal shock resistance to be achieved for the application in question. The preferable level of carbon in the matrix is less than 0.3 wt% and can be significantly lower in some applications.
The iron-base alloy can contain sufficient alloying additions for enhancement of oxidation properties and hardenability. Suitable alloying elements for these purposes include silicon, aluminium, manganese, nickel, copper and molybdenum, either separately or in combination. Preferred additions for these purposes are of silicon at up to 3 wt% such as from 0.5 to 3 wt%, aluminium at up to 0.2 wt%, manganese at up to 2 wt% such as from 0.2 to 1.5 wt%, nickel at from 0.2 to 3 wt% such as from 0.2 to 2 wt%, copper at up to 3 wt%, and/or molybdenum at up to ~ wt% such as from 0.~ to ~ wt%. The presence of silicon and/or aluminium in a melt of the iron-base alloy also is beneficial in keeping the melt in a de-oxidised condition.
The addition of molybdenum also increases hardness and improves resistance to softening at high temperatures, due to its action as a strong carbide and/or boride forming element. For the same purposes, sufficient amounts of other strong carbide and/or boride eiements, such as vanadium, titanium, tungsten and/or niobium, can be added to the iron-base alloy. Preferred additions for enhancing resistance to softening are molybdenum as indicated above, vanadium at up to 8 wt%, titanium at up to 5 wt%, niobium at up to 6 wt% and/or tungsten at up to 7 wt%.
_ Wo9~1330RO PCT~AU95tO0312
The fracture toughness, therrnal shock resistance and wear resistance of the cast ferrous alloys is largely determined by the volume fraction of hard phases, which in turn is a function of the content of both boron and carbon and carbide and boride forming elements, and also the interstitial boron and carbon content of the matrix. The boron content of the matrix is always low because thesolubility of boron in ferrite and austenite is low. tiowever the solubility of carbon in austenite and therefore the carbon content of the martensitic matrix can be as high as approximately 2 wt% unless the carbon is bound in some other phase.
It is overriding in the design of satisfactory alloy compositions for the present invention that the carbon content of the matrix is kept to a low enough level for sufficient fracture toughness or thermal shock resistance to be achieved for the application in question. The preferable level of carbon in the matrix is less than 0.3 wt% and can be significantly lower in some applications.
The iron-base alloy can contain sufficient alloying additions for enhancement of oxidation properties and hardenability. Suitable alloying elements for these purposes include silicon, aluminium, manganese, nickel, copper and molybdenum, either separately or in combination. Preferred additions for these purposes are of silicon at up to 3 wt% such as from 0.5 to 3 wt%, aluminium at up to 0.2 wt%, manganese at up to 2 wt% such as from 0.2 to 1.5 wt%, nickel at from 0.2 to 3 wt% such as from 0.2 to 2 wt%, copper at up to 3 wt%, and/or molybdenum at up to ~ wt% such as from 0.~ to ~ wt%. The presence of silicon and/or aluminium in a melt of the iron-base alloy also is beneficial in keeping the melt in a de-oxidised condition.
The addition of molybdenum also increases hardness and improves resistance to softening at high temperatures, due to its action as a strong carbide and/or boride forming element. For the same purposes, sufficient amounts of other strong carbide and/or boride eiements, such as vanadium, titanium, tungsten and/or niobium, can be added to the iron-base alloy. Preferred additions for enhancing resistance to softening are molybdenum as indicated above, vanadium at up to 8 wt%, titanium at up to 5 wt%, niobium at up to 6 wt% and/or tungsten at up to 7 wt%.
_ Wo9~1330RO PCT~AU95tO0312
-5-The iron-base alloy required for the present invention can be prepared as a melt for casting by melting suitable constituent materials in an electric induction furnace. This most preferably entails melting mild steel scrap, low carbon ferro-chromium and low carbon ferro-boron. Other commercial foundry alloys can be 5 added to provlde alloy additions required in the iron-base alloy. For re-melt charges, return scrap with about 2 wt% boron can be readily melted with mild steel scrap and ferro-alloys. The melt may be kept in a de-oxidised condition bythe use of ferro-silicon or aluminium.
The iron-base alloys of the invention have a melting point close to 1 300C.
In general, a melt pouring temperature of from 1400C to 14~0C is desirable, depending on the nature of the casting.
Subsequent to casting the iron-base alloys may be hardened by heat treating at temperatures in the range 950 to 1150C to forrn austenite and air cooling to room temperature in order to form a martensitic microstructure in thematrix of the alloy. A typical hardness after such a hardening treatment is 50 on the Rockwell C scale. If desired the iron-base alloys or a tool cast therefrom can be softened for machining by sub-critical annealing at temperatures in the range700 to 7~0C in order to decompose the matrix to a mixture of ferrite and carbide.
Such a heat treatment results in a decrease of hardness to 30 to 35 Rockwell C.
The alloys can be rehardened for service by heat treating at 9~0 to 11 50C and air cooling to provide a typical hardness of about 50 Rockwell C.
The iron-base alloy tool may be cast to near net shape by a range of casting methods depending upon the dimensional accuracy that is required and the extent to which the amount of machining to final dimensions is to be minimised.
The invention now is further illustrated by reference to the following Examples:
Fxample 1.
Blow-blow plungers come into direct contact with the molten glass as it falls into the mould, and then forces the glass into an initial shape by air pressure.
A small ledge on the tip of the plunger forms an inside rim on the neck of the bottle. This ledge on the plun~er must remain sharp so that a thin blade of glass does not form on the inside neck of the bottle.
W095/33080 PCTIAU9~/00312
The iron-base alloys of the invention have a melting point close to 1 300C.
In general, a melt pouring temperature of from 1400C to 14~0C is desirable, depending on the nature of the casting.
Subsequent to casting the iron-base alloys may be hardened by heat treating at temperatures in the range 950 to 1150C to forrn austenite and air cooling to room temperature in order to form a martensitic microstructure in thematrix of the alloy. A typical hardness after such a hardening treatment is 50 on the Rockwell C scale. If desired the iron-base alloys or a tool cast therefrom can be softened for machining by sub-critical annealing at temperatures in the range700 to 7~0C in order to decompose the matrix to a mixture of ferrite and carbide.
Such a heat treatment results in a decrease of hardness to 30 to 35 Rockwell C.
The alloys can be rehardened for service by heat treating at 9~0 to 11 50C and air cooling to provide a typical hardness of about 50 Rockwell C.
The iron-base alloy tool may be cast to near net shape by a range of casting methods depending upon the dimensional accuracy that is required and the extent to which the amount of machining to final dimensions is to be minimised.
The invention now is further illustrated by reference to the following Examples:
Fxample 1.
Blow-blow plungers come into direct contact with the molten glass as it falls into the mould, and then forces the glass into an initial shape by air pressure.
A small ledge on the tip of the plunger forms an inside rim on the neck of the bottle. This ledge on the plun~er must remain sharp so that a thin blade of glass does not form on the inside neck of the bottle.
W095/33080 PCTIAU9~/00312
-6-A blow-blow plunger tool for the manufacture of glass containers was manufactured by investment casting an iron-base alloy, within the compositional range specified above, and final machining to the exact shape required for the tool. The composition of the alloy used in this example was:
, carbon 0.2wt%
chromium 17 wt%
boron 2 wt%
silicon 0.9 wt%
manganese 0.8 wt%
molybdenum 0.5 wt%
iron remainder.
A~ter casting and prior to rough machining the plunger was sub-critically annealed at 700C for three hours to reduce the hardness to 35 Rockwell C.
Following rough machining, the plunger was heated to 950C for one hour, then cooled in air to room temperature, followed by tempering at 300C for three hours. The final hardness was 50 Rockwell C. Final machining and grinding was then done.
The blow-blow plunger manufactured in this way showed considerably improved performance over the conventional tooling made from nickel-boron 20 alloy. Conventional blow-blow plungers in this particular application have to be .
removed from service after 1 to 2 weeks continuous operation because of wear and loss of dimensional accuracy. They are then remachined before returning to service. The blow-blow plunger manufactured according to the invention remained in continuous service for 10 weeks without having to be removed for 25 remachining. This represents an improvement in the service life of the component by a factor of 5 to 10.
Fxample ~
Twenty-four plungers were made from an iron-chromium-boron alloy according to the invention, by investment casting. These were used in the 3Q production of glass containers. The plungers stayed in production for 10 to 12 weeks without having to be re-sharpened, giving a 5 to 7 times improvement in WO ~5/33080 PCTIAU~5/003 12
, carbon 0.2wt%
chromium 17 wt%
boron 2 wt%
silicon 0.9 wt%
manganese 0.8 wt%
molybdenum 0.5 wt%
iron remainder.
A~ter casting and prior to rough machining the plunger was sub-critically annealed at 700C for three hours to reduce the hardness to 35 Rockwell C.
Following rough machining, the plunger was heated to 950C for one hour, then cooled in air to room temperature, followed by tempering at 300C for three hours. The final hardness was 50 Rockwell C. Final machining and grinding was then done.
The blow-blow plunger manufactured in this way showed considerably improved performance over the conventional tooling made from nickel-boron 20 alloy. Conventional blow-blow plungers in this particular application have to be .
removed from service after 1 to 2 weeks continuous operation because of wear and loss of dimensional accuracy. They are then remachined before returning to service. The blow-blow plunger manufactured according to the invention remained in continuous service for 10 weeks without having to be removed for 25 remachining. This represents an improvement in the service life of the component by a factor of 5 to 10.
Fxample ~
Twenty-four plungers were made from an iron-chromium-boron alloy according to the invention, by investment casting. These were used in the 3Q production of glass containers. The plungers stayed in production for 10 to 12 weeks without having to be re-sharpened, giving a 5 to 7 times improvement in WO ~5/33080 PCTIAU~5/003 12
- 7 -production life compared with plungers of a conventional nickel-boron alloy. Theparticular composition for these plungers was as follows:
Carbon 0.23%
Silicon 1.07%
Manganese 1.1 1%
Phosphorous 0.017%
Sulphur 0.017%
Chromium 14.7~3%
Molybdenum 0.40%
Nickel 1.~0%
Copper 0. 14%
Aluminium 0.096%
Niobium 0. 175%
Boron 2.0%
Balance mainly iron A small amount of niobium was added to precipitate small niobium carbides, to improve wear resistance.
~xample 3 Guide plate castings are solid flat discs with a central hole through which a plunger will pass and retract. The clearance between the plunger and the centralhole is critical and should not be allowed to become large enough to allow molten glass to penetrate between the plunger and the guide plate. Wear between the plunger and the guide plate at temperatures up to 500C is the main cause of replacement of the guide plate.
Twenty guide plates made from the iron-chromium-boron alloy by investment casting have been trialed in production of a ~00 ml bottle for 13 days continuously with no measurable change in dimension. Guide plates made from nickel-boron alloy or tool steel require measurement after seven days and generally approximately half are rejected because tolerances are exceeded because of wear. The composition of the iron-chromium-boron guide plates was as follows:
Carbon 0.28% by weight W O ~5133080 PCTtA U9~1003 12
Carbon 0.23%
Silicon 1.07%
Manganese 1.1 1%
Phosphorous 0.017%
Sulphur 0.017%
Chromium 14.7~3%
Molybdenum 0.40%
Nickel 1.~0%
Copper 0. 14%
Aluminium 0.096%
Niobium 0. 175%
Boron 2.0%
Balance mainly iron A small amount of niobium was added to precipitate small niobium carbides, to improve wear resistance.
~xample 3 Guide plate castings are solid flat discs with a central hole through which a plunger will pass and retract. The clearance between the plunger and the centralhole is critical and should not be allowed to become large enough to allow molten glass to penetrate between the plunger and the guide plate. Wear between the plunger and the guide plate at temperatures up to 500C is the main cause of replacement of the guide plate.
Twenty guide plates made from the iron-chromium-boron alloy by investment casting have been trialed in production of a ~00 ml bottle for 13 days continuously with no measurable change in dimension. Guide plates made from nickel-boron alloy or tool steel require measurement after seven days and generally approximately half are rejected because tolerances are exceeded because of wear. The composition of the iron-chromium-boron guide plates was as follows:
Carbon 0.28% by weight W O ~5133080 PCTtA U9~1003 12
- 8 -Silicon 1. 13%
Manganese 1. 15%
Phosphorous 0.017%
Sulphur 0.014%
Chromium 14.6%
Molybdenum 0.73%
Nickel 1.83%
Copper 0.14%
Aluminium 0.026%
Boron 2.0%
Balance mainly iron Example 4 Thimbles are castings shaped like a top hat which are part of the support mechanism of the bottle mould. The main reason for replacement of the thimble 15 is wear on the top horizontal face and wear in the bore. The thimbles are usually made from nickel-boron alloy or tool steel and after two to three weeks of continuous operation are removed and checked for wear.
If the two dimensions are worn more than 0.005 inches (0.13 mm), then they are scrapped. Most thimbles of conventional nickel-boron alloy last four to20 six weeks.
A trial with iron-chromium-boron thimbles manufactured by investment casting showed 0.08 mm (0.003 inches) wear on the flat horizontal face and 0.06 mm (0.0025 inches) wear in the bore after eleven weeks continuous service.
There is considerable improvement in wear resistance of the new invented alloy 25 compared with presently used alloys. The composition of the iron-chromium-boron thimbles was as follows:
Carbon 0.29% by weight Silicon 1.03%
Manganese 1. 13%
Phosphorous O.Q09%
Sulphur 0.01 2%
Nickel 2.08%
wo ~5/33080 2 1 9 0 9 5 3 PCT/AU95/00312
Manganese 1. 15%
Phosphorous 0.017%
Sulphur 0.014%
Chromium 14.6%
Molybdenum 0.73%
Nickel 1.83%
Copper 0.14%
Aluminium 0.026%
Boron 2.0%
Balance mainly iron Example 4 Thimbles are castings shaped like a top hat which are part of the support mechanism of the bottle mould. The main reason for replacement of the thimble 15 is wear on the top horizontal face and wear in the bore. The thimbles are usually made from nickel-boron alloy or tool steel and after two to three weeks of continuous operation are removed and checked for wear.
If the two dimensions are worn more than 0.005 inches (0.13 mm), then they are scrapped. Most thimbles of conventional nickel-boron alloy last four to20 six weeks.
A trial with iron-chromium-boron thimbles manufactured by investment casting showed 0.08 mm (0.003 inches) wear on the flat horizontal face and 0.06 mm (0.0025 inches) wear in the bore after eleven weeks continuous service.
There is considerable improvement in wear resistance of the new invented alloy 25 compared with presently used alloys. The composition of the iron-chromium-boron thimbles was as follows:
Carbon 0.29% by weight Silicon 1.03%
Manganese 1. 13%
Phosphorous O.Q09%
Sulphur 0.01 2%
Nickel 2.08%
wo ~5/33080 2 1 9 0 9 5 3 PCT/AU95/00312
9 _ Chromium 1 7.38%
Molybdenum 1. 12%
Copper 0. 1~%
Aluminium 0.026%
~oron 2.0%
E~alance mainly iron In this case, molybdenum was increased to over one per cent in order to improve hot hardness.
Finally, it is to be understood that various alterations, modifications and/or
Molybdenum 1. 12%
Copper 0. 1~%
Aluminium 0.026%
~oron 2.0%
E~alance mainly iron In this case, molybdenum was increased to over one per cent in order to improve hot hardness.
Finally, it is to be understood that various alterations, modifications and/or
10 additions may be introduced into the constructions and arrangements of parts previously described without departing from the spirit or ambit of the invention.
Claims (14)
1. A tool for use in contact with molten glass in the manufacture of glass containers, wherein said tool is cast from an alloy having:
from 1 to 20 wt% chromium and from 0.5 to 3 wt% boron, the alloy optionally containing carbon subject to carbon in excess of 1.0 wt% being bound by at leastone strong carbide forming element in a carbide and/or carbo-boride phase and the alloy otherwise optionally including said at least one carbide forming element, and wherein the alloy further contains:
0 to 3 wt% silicon, 0 to 0.2 wt% aluminium, 0 to 2 wt% manganese, 0 to 3 wt% nickel, 0 to 3 wt% copper, 0 to 5 wt% molybdenum and a balance apart from incidental impurities of iron.
from 1 to 20 wt% chromium and from 0.5 to 3 wt% boron, the alloy optionally containing carbon subject to carbon in excess of 1.0 wt% being bound by at leastone strong carbide forming element in a carbide and/or carbo-boride phase and the alloy otherwise optionally including said at least one carbide forming element, and wherein the alloy further contains:
0 to 3 wt% silicon, 0 to 0.2 wt% aluminium, 0 to 2 wt% manganese, 0 to 3 wt% nickel, 0 to 3 wt% copper, 0 to 5 wt% molybdenum and a balance apart from incidental impurities of iron.
2 A tool according to claim 1, wherein the tool in its as cast condition, following air-cooling, has a matrix exhibiting a martensitic structure.
3. A tool according to claim 1, wherein the tool has a matrix with a martensiticstructure produced by heat treatment at from 950 to 1150° to form austenite, followled by air cooling to provide the martensitic microstructure.
4. A tool according to claim 1, wherein the tool in an as cast condition has been softened by annealing at from 700 to 750°C, then machined to final shape, then heat treated at from 950 to 1150°C to form austenite, and then air cooled to provide a martensitic microstructure.
. A tool according to claim 1, wherein said tool has a hardness of about 50 on the Rochwell C scale.
6. A tool according to claim 1, wherein the matrix has less than 0.3 wt%
carbon.
carbon.
7. A tool according to claim 1, wherein the carbon content does not exceed 0.60 wt%.
8. A tool according to claim 7, wherein the carbon content is from 0.1 to 0.3 wt%.
9. A tool according to claim 1, wherein the boron content is from 1 to 2.5 wt%
.
.
10. A tool according to claim 1, wherein the chromium content is from 3 to 18 wt%.
11. A tool according to claim 10, wherein the chromium content is from 8 to 18wt%.
12. A tool according to claim 1, wherein the chromium content is such that the alloy has a high chromium content matrix which is hardenable to martensite with heat treatment .
13. A tool according to claim 1, wherein said alloy contains at least one of silicon, aluminium, manganese, nickel, copper and molybdenum at a respective content of:
silicon 0.5 to 3 wt%
aluminium up to 0.2 wt%
manganese 0.2 to 1.5 wt%
nickel 0.2 to 2 wt%
copper up to 3 wt%
molybdenum 0.5 to 5 wt%
silicon 0.5 to 3 wt%
aluminium up to 0.2 wt%
manganese 0.2 to 1.5 wt%
nickel 0.2 to 2 wt%
copper up to 3 wt%
molybdenum 0.5 to 5 wt%
14. A tool according to claim 1, wherein said alloy contains at least one of molybdenum, vanadium, titanium, tungsten and niobium to improve resistance to softening at high temperatures, due to action as a strong carbide and/or boride forming element, at a respective content of:
molybdenurn 0.5 to 5 wt%
vanadium up to 8 wt%
titanium up to 5 wt%
tungsten up to 7 wt%
niobium up to 6 wt%.
molybdenurn 0.5 to 5 wt%
vanadium up to 8 wt%
titanium up to 5 wt%
tungsten up to 7 wt%
niobium up to 6 wt%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AUPM5930A AUPM593094A0 (en) | 1994-05-30 | 1994-05-30 | Tools for the manufacture of glass articles |
| AUPM5930 | 1994-05-30 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2190953A1 true CA2190953A1 (en) | 1995-12-07 |
Family
ID=3780505
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002190953A Abandoned CA2190953A1 (en) | 1994-05-30 | 1995-05-29 | Iron-chromium-boron alloy for glass manufacturing tools |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0763142A4 (en) |
| JP (1) | JPH10500735A (en) |
| CN (1) | CN1149322A (en) |
| AU (1) | AUPM593094A0 (en) |
| CA (1) | CA2190953A1 (en) |
| WO (1) | WO1995033080A1 (en) |
| ZA (1) | ZA954364B (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6110300A (en) * | 1997-04-07 | 2000-08-29 | A. Finkl & Sons Co. | Tool for glass molding operations and method of manufacture thereof |
| JP4778735B2 (en) | 2005-06-24 | 2011-09-21 | 東芝機械株式会社 | Manufacturing method of glass mold |
| DE112008000947B4 (en) | 2007-04-10 | 2012-01-19 | Toshiba Kikai K.K. | Glass forming mold |
| CN106167876A (en) * | 2016-07-01 | 2016-11-30 | 宜兴市凯诚模具有限公司 | A kind of glass alloy mould and manufacture method thereof |
| US20210189514A1 (en) * | 2018-09-07 | 2021-06-24 | Milson Foundry Nz Limited | Steel alloy |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1493191A (en) * | 1922-11-16 | 1924-05-06 | Golyer Anthony G De | Alloy |
| GB1505841A (en) * | 1974-01-12 | 1978-03-30 | Watanabe H | Iron-chromium amorphous alloys |
| US4140525A (en) * | 1978-01-03 | 1979-02-20 | Allied Chemical Corporation | Ultra-high strength glassy alloys |
| US4362553A (en) * | 1979-11-19 | 1982-12-07 | Marko Materials, Inc. | Tool steels which contain boron and have been processed using a rapid solidification process and method |
| US4318733A (en) * | 1979-11-19 | 1982-03-09 | Marko Materials, Inc. | Tool steels which contain boron and have been processed using a rapid solidification process and method |
| JPS59104454A (en) * | 1982-12-02 | 1984-06-16 | Nissan Motor Co Ltd | Anti-wear sintered alloy |
| ZA934072B (en) * | 1992-06-19 | 1994-01-19 | Commw Scient Ind Res Org | Rolls for metal shaping |
-
1994
- 1994-05-30 AU AUPM5930A patent/AUPM593094A0/en not_active Abandoned
-
1995
- 1995-05-29 ZA ZA954364A patent/ZA954364B/en unknown
- 1995-05-29 CA CA002190953A patent/CA2190953A1/en not_active Abandoned
- 1995-05-29 CN CN95193342A patent/CN1149322A/en active Pending
- 1995-05-29 WO PCT/AU1995/000312 patent/WO1995033080A1/en not_active Application Discontinuation
- 1995-05-29 EP EP95919929A patent/EP0763142A4/en not_active Withdrawn
- 1995-05-29 JP JP8500075A patent/JPH10500735A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| ZA954364B (en) | 1996-02-19 |
| JPH10500735A (en) | 1998-01-20 |
| AUPM593094A0 (en) | 1994-06-23 |
| CN1149322A (en) | 1997-05-07 |
| EP0763142A4 (en) | 1997-09-17 |
| WO1995033080A1 (en) | 1995-12-07 |
| EP0763142A1 (en) | 1997-03-19 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FZDE | Discontinued |