CA1119850A - Roll for hot forming steel rod - Google Patents
Roll for hot forming steel rodInfo
- Publication number
- CA1119850A CA1119850A CA000340553A CA340553A CA1119850A CA 1119850 A CA1119850 A CA 1119850A CA 000340553 A CA000340553 A CA 000340553A CA 340553 A CA340553 A CA 340553A CA 1119850 A CA1119850 A CA 1119850A
- Authority
- CA
- Canada
- Prior art keywords
- carbide
- per cent
- volume
- roll
- binder alloy
- 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
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
Abstract
TITLE OF THE INVENTION
ROLL FOR HOT FORMING STEEL ROD
ABSTRACT OF THE DISCLOSURE
Disclosed herein is a carbide roll having an improved composition for hot forming steel rod in multi-stand rolling mills. The improved composition comprises the addition of tantalum carbide to a normal tungsten carbide-cobalt roll composition, preferably, so that the composition by volume is approximately: tungsten carbide--65 per cent; tantalum carbide--12 per cent; and cobalt--23 per cent. A dual composition is preferable, wherein the above composition forms the outer layer of the roll and an inner layer is composed of, by volume, tungsten carbide--76 per cent and cobalt--24 per cent,
ROLL FOR HOT FORMING STEEL ROD
ABSTRACT OF THE DISCLOSURE
Disclosed herein is a carbide roll having an improved composition for hot forming steel rod in multi-stand rolling mills. The improved composition comprises the addition of tantalum carbide to a normal tungsten carbide-cobalt roll composition, preferably, so that the composition by volume is approximately: tungsten carbide--65 per cent; tantalum carbide--12 per cent; and cobalt--23 per cent. A dual composition is preferable, wherein the above composition forms the outer layer of the roll and an inner layer is composed of, by volume, tungsten carbide--76 per cent and cobalt--24 per cent,
Description
~9~o BACKGROUND OF THE INVENTION
This invention concerns cemented carbide rolls for hot-forming steel rod in multi-stand rolling mills, especially in a finished rod diameter range of 7/32 inches to 1/2 inch.
Carbide rolls, operating at rod temperatures typically in the 1700F to 2200F range, have gained wide use in multi-stand steel-rod rolling mills and, to a large extent, have replaced chilled cast iron rolls, especially in finishing roll mill stands.
The development of twist free rod mills allowed the use of higher, more economical hot rolling speeds without sacrifice of rod product dimensions or rod surface condition. The successful introduction of cemented carbide rolls of homogeneous, single-composition, tungsten carbide-cobalt alloys provided a roll material capable of being designed to withstand higher rolling speeds.
The sole hard carbide constituent in these roll alloys preferred by those skilled in the art, and most successful in application, has been tungsten carbide (WC), without additions of other hard carbides, such as tantalum carbide, tantalum carbide-niobium carbide solid solution, niobium carbide, titanium carbide or tungsten carbide-titanium carbide solid solution. The addition of such carbides is widely believed to impair mechanical wear properties and mechanical toughness, both desirable properties în hot steel rod mill rolls.
The realization of the benefits of still greater rolling speeds of which improved mill design is now capable, however, requires roll materials possessing more resistance to wear induced by thermal fatigue. Both the surface degradation of roll groove surfaces, or other working surface configuration, and massive roll fracture are related to several factors, among which a major factor is thermal cracking caused by alternate heating and cooling of the mill roll as it encounters the hot steel rod.
Thermal crack patterns on used carbide roll groove, or working, surfaces occur at every stage of the reduction process.
As heat cracks form and propagate vertically downward into the subsurface carbide, the exposure of newly created carbide surfaces to cooling water which becomes hot and steam enables leaching of the cobalt binder from the crack areas of the cemented carbide roll to occur.
As thermal cracks are deepened by the twin forces of thermal crack propagation and leaching, the roll working surface wear rate increases and the rolled rod surface condition deteriorates requiring removal of the roll for grinding off the surface damage. As surface condition of rolled rod or rod dimensions approach tolerance, the roll working surfaces are ground to completely remove thermal cracks prior to reuse.
Massive fracture of the roll caused by a splitting action initiated by thermal cracks may also occur.
Rolls used for slower rolling speeds and larger rolling diameters, such as pre-finishing mills and bar mills having a finished rod diameter of 1/2 inch to three inches, are subject to even greater thermal stress because thermal cycling is accelerated by longer time intervals of roll-to work contact and cooling exposure.
Thermal cracking of working surfaces, therefore, operates as a catalyst of wear, a cause of fracture failure, and a cause of surface roughness of the rolled rod.
It is an object of this invention to provide a cemented carbide roll for hot forming steel rod in multi-stand rod or bar mills which is significantly more resistant to thermal cracking.
It is an additional object of this invention to provide a roll which possesses greater resistance to surface wear and cobalt binder leaching as evidenced by longer roll service time and greater steel tonnage rolled before removal of the roll from the mill for grinding.
BRIEF SUMMARY OF THE ~NVENTION
According to the present invention, a cemented carbide roll can have the thermal fatigue and wear resistant properties increased by the addition of tantalum carbide to the roll composition. Preferably, the composition of the roll near its outer working surface will comprise, by volume: tungsten carbide--65 per cent; tantalum carbide--l~ per cent; and cobalt--23 per cent; however, the composition may be in the range, by volume, of: tungsten carbide--45 to 72 per cent;
tantalum carbide--5 to 13 per cent; and cobalt--23 to 42 per cent.
Because of the cost of the tantalum carbide, which is approximately two or three times that of tungsten carbide, it is somewhat more economical to make a d~al compact roll with an 98~
outer layer as described above, but with an inner layer preferably comprised of, by volume, 76 per cent tungsten carbide and 24 per cent cobalt. The inner layer, however, may be in the range of, by volume, 24 to 43 per cent cobalt, and the balance tungsten carbide.
DETAILED DESCRIPTION OF THE INVENTION
The invention is achieved by constructing a dual-composition carbide roll consisting of a longer-wearing peripheral or outer cemented carbide zone in which the rolling grooves, or working surfaces, are formed and possessing excep~ional thermal fatigue and wear resistance derived from the incorporation of tantalum carbide (TaC) in a tungsten carbide (WC)-cobalt (Co) base composition, and a mechanically tough inner support core of tungsten carbide-cobalt composition possessing a binder volume and carbide grain structure identical with or similar to that which exists in the peripheral or outer zone.
Both zones form a solid, integrated roll body with a sinter-bonded interface. Carbide-robalt powder blends suitable for each zone are first pressed together in a powder compacting press, then sintered together as a single pressing. The use of tantalum carbide, which is normally higher in cost than is tungsten carbide, is thus restricted to the critical peripheral working zone of the roll, thereby limiting its use and yet gaining a substantial improvement in acceptable service life between regrinds of the rolling groove.
The improved mill roll possesses as its principal and critical feature a dual-composition cemented carbide structure, of which the outer or rolling zone consists of a tungsten carbide-tantalum carbide-cobalt cemented carbide composition and an inner or core zone of cemented tungsten carbide-cobalt having identical or similar volume per cent of binder metal.
It is recognized that dissimilarities between the zones in carbide grain size range, volume per cent of bindex and binder composition may not cause an unacceptable rate of fracture failure of the roll because of inherent differences in thermal coefficient of e~pansion between the zones, either in use or during manufacture. Nevertheless, identical or similar per cent binder volumes, carbide grain size ranges and binder compositions in the outer and inner zones are a preferred embodiment of this invention.
Two 8.125 inch diameter single-groove identical cemented carbide rolls were made having an outer zone composition in terms of per cent by volume of tungsten carbide--65 per cent;
tantalum carbide--12 per cent; and cobalt--23 per cent, integrated by means of a sinter-bonded interface with an inner cemented carbide core zone having a composition in per cent by vol~me of tungsten carbide--76 per cent and cobalt--24 per cent.
Both zones were made to have a tungsten carbide grain size range of approximately 90 per cent 3 to 12 micron and a tantalum carbide grain size range of approximately 90 per cent 3 to 6 micron after sintering. The design density of the outer zone was 13 79 grams per cubic centimeter and of the inner zone 13.95 grams per cubic centimeter. The outer or rolling zone was 1.125 inches thick, just sufficient to provide for outer ~1~9~50 zone material both to accommodate the forming of the rolling groove and the subsequent grinding of the groove between roll passesl, but without unnecessary or excessive thickness, so as to achie~e the greatest possible economy in the use of tantalum carbide.
The best 8 and 1/8 inches diameter cemented carbide finishing rolls containing, in terms of per cent by volume, 23 to 25 per cent cobalt and 75 to 77 per cent of tungsten carbide with a sintered grain size range of approximately 90 per cent 3 to 12 microns typically attain about 72 tons of steel rod production per 0.091 inches of grinding removal on the roll diameter. By comparison, the dual composition 8 and 1/8 inches finishing rolls operating in the same position and under equivalent rolling conditions achieved about 100 tons per 0.001 inches grinding removal on the first pass before the rolls were removed from the roll stand for grinding to remove thermal damage to the rolling groove surfaces. This represents a 40 per cent increase in roll service life and a significant increase in mill utilization efficiency by lessening the frequency of mill shutdowns for changing rolls.
Carbide grain size ranges typically used in rolls in accord with the current art vary according to the precepts of manufacturers; it is recognized that at least some of the economic benefit of this invention will occur independently of grain size ranges employed in the peripheral and inner zones.
Similarly, it may be foreseen that substitutions for tantalum carbide, all or in part, by binary or ternary soLid lil~BS(~
solution carbides involving combinations of niobium, tantalum or hafnium, or by the monocarbides of niobium or hafnium in the peripheral or outer zone may achieve at least part of the economic benefit of this invention, owing to the relatively good thermal crack resistance of these carbides. However, tantalum carbide is a preferred embodiment of this invention because its specific gravity is very close to that of tungsten carbide thereby facilitatingg as between the outer and inner zones, nearly equal shrinkage during sintering and nearly equal binder volumes and sintered densities when equal weight percentages of binder are used in the powder blend compositions, also because tantalum carbide possesses excellent resistance to heat cracking among all the hard carbides.
An incorporation of tantalum carbide, as an important hot steel rod mill roll constituent, is, in itself, both novel and useful regardless of the important economy realized from a dual-composition roll. Therefore, it follows that a single composition roll having the same composition throughout as the peripheral zone will possess some, if not all, of the benefits of a dual-composition roll.
It is understood that the volume per cent of binder, as well as the binder composition, and the volume percentage of tantalum carbide, may be altered in either or both zones without impairing some or any of the economic benefits of this invention, and that, further, the benefits of this invention can be realized in hot rolling metals and compositions other than steel.
Modifications may be made within the scope of the appended claims.
_g_
This invention concerns cemented carbide rolls for hot-forming steel rod in multi-stand rolling mills, especially in a finished rod diameter range of 7/32 inches to 1/2 inch.
Carbide rolls, operating at rod temperatures typically in the 1700F to 2200F range, have gained wide use in multi-stand steel-rod rolling mills and, to a large extent, have replaced chilled cast iron rolls, especially in finishing roll mill stands.
The development of twist free rod mills allowed the use of higher, more economical hot rolling speeds without sacrifice of rod product dimensions or rod surface condition. The successful introduction of cemented carbide rolls of homogeneous, single-composition, tungsten carbide-cobalt alloys provided a roll material capable of being designed to withstand higher rolling speeds.
The sole hard carbide constituent in these roll alloys preferred by those skilled in the art, and most successful in application, has been tungsten carbide (WC), without additions of other hard carbides, such as tantalum carbide, tantalum carbide-niobium carbide solid solution, niobium carbide, titanium carbide or tungsten carbide-titanium carbide solid solution. The addition of such carbides is widely believed to impair mechanical wear properties and mechanical toughness, both desirable properties în hot steel rod mill rolls.
The realization of the benefits of still greater rolling speeds of which improved mill design is now capable, however, requires roll materials possessing more resistance to wear induced by thermal fatigue. Both the surface degradation of roll groove surfaces, or other working surface configuration, and massive roll fracture are related to several factors, among which a major factor is thermal cracking caused by alternate heating and cooling of the mill roll as it encounters the hot steel rod.
Thermal crack patterns on used carbide roll groove, or working, surfaces occur at every stage of the reduction process.
As heat cracks form and propagate vertically downward into the subsurface carbide, the exposure of newly created carbide surfaces to cooling water which becomes hot and steam enables leaching of the cobalt binder from the crack areas of the cemented carbide roll to occur.
As thermal cracks are deepened by the twin forces of thermal crack propagation and leaching, the roll working surface wear rate increases and the rolled rod surface condition deteriorates requiring removal of the roll for grinding off the surface damage. As surface condition of rolled rod or rod dimensions approach tolerance, the roll working surfaces are ground to completely remove thermal cracks prior to reuse.
Massive fracture of the roll caused by a splitting action initiated by thermal cracks may also occur.
Rolls used for slower rolling speeds and larger rolling diameters, such as pre-finishing mills and bar mills having a finished rod diameter of 1/2 inch to three inches, are subject to even greater thermal stress because thermal cycling is accelerated by longer time intervals of roll-to work contact and cooling exposure.
Thermal cracking of working surfaces, therefore, operates as a catalyst of wear, a cause of fracture failure, and a cause of surface roughness of the rolled rod.
It is an object of this invention to provide a cemented carbide roll for hot forming steel rod in multi-stand rod or bar mills which is significantly more resistant to thermal cracking.
It is an additional object of this invention to provide a roll which possesses greater resistance to surface wear and cobalt binder leaching as evidenced by longer roll service time and greater steel tonnage rolled before removal of the roll from the mill for grinding.
BRIEF SUMMARY OF THE ~NVENTION
According to the present invention, a cemented carbide roll can have the thermal fatigue and wear resistant properties increased by the addition of tantalum carbide to the roll composition. Preferably, the composition of the roll near its outer working surface will comprise, by volume: tungsten carbide--65 per cent; tantalum carbide--l~ per cent; and cobalt--23 per cent; however, the composition may be in the range, by volume, of: tungsten carbide--45 to 72 per cent;
tantalum carbide--5 to 13 per cent; and cobalt--23 to 42 per cent.
Because of the cost of the tantalum carbide, which is approximately two or three times that of tungsten carbide, it is somewhat more economical to make a d~al compact roll with an 98~
outer layer as described above, but with an inner layer preferably comprised of, by volume, 76 per cent tungsten carbide and 24 per cent cobalt. The inner layer, however, may be in the range of, by volume, 24 to 43 per cent cobalt, and the balance tungsten carbide.
DETAILED DESCRIPTION OF THE INVENTION
The invention is achieved by constructing a dual-composition carbide roll consisting of a longer-wearing peripheral or outer cemented carbide zone in which the rolling grooves, or working surfaces, are formed and possessing excep~ional thermal fatigue and wear resistance derived from the incorporation of tantalum carbide (TaC) in a tungsten carbide (WC)-cobalt (Co) base composition, and a mechanically tough inner support core of tungsten carbide-cobalt composition possessing a binder volume and carbide grain structure identical with or similar to that which exists in the peripheral or outer zone.
Both zones form a solid, integrated roll body with a sinter-bonded interface. Carbide-robalt powder blends suitable for each zone are first pressed together in a powder compacting press, then sintered together as a single pressing. The use of tantalum carbide, which is normally higher in cost than is tungsten carbide, is thus restricted to the critical peripheral working zone of the roll, thereby limiting its use and yet gaining a substantial improvement in acceptable service life between regrinds of the rolling groove.
The improved mill roll possesses as its principal and critical feature a dual-composition cemented carbide structure, of which the outer or rolling zone consists of a tungsten carbide-tantalum carbide-cobalt cemented carbide composition and an inner or core zone of cemented tungsten carbide-cobalt having identical or similar volume per cent of binder metal.
It is recognized that dissimilarities between the zones in carbide grain size range, volume per cent of bindex and binder composition may not cause an unacceptable rate of fracture failure of the roll because of inherent differences in thermal coefficient of e~pansion between the zones, either in use or during manufacture. Nevertheless, identical or similar per cent binder volumes, carbide grain size ranges and binder compositions in the outer and inner zones are a preferred embodiment of this invention.
Two 8.125 inch diameter single-groove identical cemented carbide rolls were made having an outer zone composition in terms of per cent by volume of tungsten carbide--65 per cent;
tantalum carbide--12 per cent; and cobalt--23 per cent, integrated by means of a sinter-bonded interface with an inner cemented carbide core zone having a composition in per cent by vol~me of tungsten carbide--76 per cent and cobalt--24 per cent.
Both zones were made to have a tungsten carbide grain size range of approximately 90 per cent 3 to 12 micron and a tantalum carbide grain size range of approximately 90 per cent 3 to 6 micron after sintering. The design density of the outer zone was 13 79 grams per cubic centimeter and of the inner zone 13.95 grams per cubic centimeter. The outer or rolling zone was 1.125 inches thick, just sufficient to provide for outer ~1~9~50 zone material both to accommodate the forming of the rolling groove and the subsequent grinding of the groove between roll passesl, but without unnecessary or excessive thickness, so as to achie~e the greatest possible economy in the use of tantalum carbide.
The best 8 and 1/8 inches diameter cemented carbide finishing rolls containing, in terms of per cent by volume, 23 to 25 per cent cobalt and 75 to 77 per cent of tungsten carbide with a sintered grain size range of approximately 90 per cent 3 to 12 microns typically attain about 72 tons of steel rod production per 0.091 inches of grinding removal on the roll diameter. By comparison, the dual composition 8 and 1/8 inches finishing rolls operating in the same position and under equivalent rolling conditions achieved about 100 tons per 0.001 inches grinding removal on the first pass before the rolls were removed from the roll stand for grinding to remove thermal damage to the rolling groove surfaces. This represents a 40 per cent increase in roll service life and a significant increase in mill utilization efficiency by lessening the frequency of mill shutdowns for changing rolls.
Carbide grain size ranges typically used in rolls in accord with the current art vary according to the precepts of manufacturers; it is recognized that at least some of the economic benefit of this invention will occur independently of grain size ranges employed in the peripheral and inner zones.
Similarly, it may be foreseen that substitutions for tantalum carbide, all or in part, by binary or ternary soLid lil~BS(~
solution carbides involving combinations of niobium, tantalum or hafnium, or by the monocarbides of niobium or hafnium in the peripheral or outer zone may achieve at least part of the economic benefit of this invention, owing to the relatively good thermal crack resistance of these carbides. However, tantalum carbide is a preferred embodiment of this invention because its specific gravity is very close to that of tungsten carbide thereby facilitatingg as between the outer and inner zones, nearly equal shrinkage during sintering and nearly equal binder volumes and sintered densities when equal weight percentages of binder are used in the powder blend compositions, also because tantalum carbide possesses excellent resistance to heat cracking among all the hard carbides.
An incorporation of tantalum carbide, as an important hot steel rod mill roll constituent, is, in itself, both novel and useful regardless of the important economy realized from a dual-composition roll. Therefore, it follows that a single composition roll having the same composition throughout as the peripheral zone will possess some, if not all, of the benefits of a dual-composition roll.
It is understood that the volume per cent of binder, as well as the binder composition, and the volume percentage of tantalum carbide, may be altered in either or both zones without impairing some or any of the economic benefits of this invention, and that, further, the benefits of this invention can be realized in hot rolling metals and compositions other than steel.
Modifications may be made within the scope of the appended claims.
_g_
Claims (7)
1. An improved carbide hot roll comprising: an outer cemented carbide working layer surrounding and bonded to a cemented carbide inner layer; said outer cemented carbide working layer is homogeneous and is comprised of 45 to 72 per cent by volume tungsten carbide, 23 to 42 per cent by volume of a binder alloy, and 5 to 13 volume per cent of a thermal cracking resistant carbide selected from the group consisting of tantalum carbide, niobium carbide, hafnium carbide, their solid solutions and their mixtures; said inner cemented carbide layer comprising 23 to 42 volume per cent of a second binder alloy with the balance being tungsten carbide;
said binder alloy used in said outer cemented carbide working layer and said second binder alloy used in said inner layer have equivalent compositions and makeup similar volume percen-tages of their respective layers; said outer cemented carbide working layer having a first and second carbide grain size range respectively; and wherein said first and second grain size ranges are similar and define an average grain size of between 3 to 12 microns.
said binder alloy used in said outer cemented carbide working layer and said second binder alloy used in said inner layer have equivalent compositions and makeup similar volume percen-tages of their respective layers; said outer cemented carbide working layer having a first and second carbide grain size range respectively; and wherein said first and second grain size ranges are similar and define an average grain size of between 3 to 12 microns.
2. An improved carbide hot roll comprising a homogeneous outer working layer comprised of tungsten carbide, and a thermal cracking resistant carbide selected from the group consisting of tantalum carbide, niobium carbide, hafnium carbide, their solid solutions and their mixtures in the range of: tungsten carbide--45 to 72 per cent by volume; thermal cracking resistant carbide--5 to 13 per cent by volume;
binder alloy--23 to 42 per cent by volume; an inner layer of carbide material inwardly of the material around said outer working layer and bonded to said outer working layer, said inner layer comprising tungsten carbide and a second binder alloy in the ranges of: second binder alloy--23 to 42 per cent by volume; tungsten carbide---balance.
binder alloy--23 to 42 per cent by volume; an inner layer of carbide material inwardly of the material around said outer working layer and bonded to said outer working layer, said inner layer comprising tungsten carbide and a second binder alloy in the ranges of: second binder alloy--23 to 42 per cent by volume; tungsten carbide---balance.
3. An improved carbide hot roll according to Claims 1 or 2 wherein said thermal cracking resistant carbide is tantalum carbide.
4. An improved carbide hot roll according to Claims 1 or 2 wherein said binder alloy is selected from the group consisting of cobalt and cobalt based alloys.
5. An improved carbide hot roll according to Claim 2 wherein said binder alloy used in said outer working layer material and said second binder alloy used in said inner layer have equivalent compositions.
6. An improved carbide hot roll according to Claim 5 wherein said per cent by volume of said binder alloy and said per cent by volume of said second binder are equivalent.
7. An improved carbide hot roll according to Claims 1 or 2 further comprised of an equivalence of carbide grain size ranges containing approximately 90 per cent of the carbide grains found in the outer working layer material and the inner layer.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US96585978A | 1978-12-04 | 1978-12-04 | |
| US965,859 | 1978-12-04 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1119850A true CA1119850A (en) | 1982-03-16 |
Family
ID=25510598
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000340553A Expired CA1119850A (en) | 1978-12-04 | 1979-11-23 | Roll for hot forming steel rod |
Country Status (6)
| Country | Link |
|---|---|
| JP (1) | JPS5594457A (en) |
| CA (1) | CA1119850A (en) |
| DE (1) | DE2948783C2 (en) |
| FR (1) | FR2443294A1 (en) |
| GB (1) | GB2036620B (en) |
| IT (1) | IT1125899B (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5541006A (en) * | 1994-12-23 | 1996-07-30 | Kennametal Inc. | Method of making composite cermet articles and the articles |
| US5677042A (en) * | 1994-12-23 | 1997-10-14 | Kennametal Inc. | Composite cermet articles and method of making |
| US5686119A (en) * | 1994-12-23 | 1997-11-11 | Kennametal Inc. | Composite cermet articles and method of making |
| US6908688B1 (en) | 2000-08-04 | 2005-06-21 | Kennametal Inc. | Graded composite hardmetals |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE120441T1 (en) * | 1983-03-28 | 1985-08-14 | Kennametal Inc., Latrobe, Pa. | ROLL FOR HOT ROLLING STEEL. |
| US4698884A (en) * | 1983-03-28 | 1987-10-13 | Kennametal Inc. | Roll for hot forming steel rod |
| JPS6146307A (en) * | 1984-08-10 | 1986-03-06 | Sumitomo Metal Ind Ltd | Build-up roll and its manufacture |
| FI70273C (en) * | 1985-01-09 | 1986-09-15 | Valmet Oy | SYNTHETIC PRESS RELEASES FOR THE FRAMEWORK OF THE FRAMEWORK |
| US4866968A (en) * | 1987-06-17 | 1989-09-19 | Westinghouse Electric Corp. | High strength cemented carbide dies and mandrels for a pilgering machine |
| SE469822B (en) * | 1992-02-07 | 1993-09-27 | Sandvik Ab | Tungsten carbide for rolling metal strips and wire plate |
| SE517473C2 (en) * | 1996-07-19 | 2002-06-11 | Sandvik Ab | Roll for hot rolling with resistance to thermal cracks and wear |
| MX2016011785A (en) | 2014-03-14 | 2016-12-02 | Sandvik Intellectual Property | Compound roll. |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE615262C (en) * | 1934-01-24 | 1935-07-01 | Fried Krupp Akt Ges | Drawing die made from a hard metal alloy |
| US2053997A (en) * | 1935-04-19 | 1936-09-08 | Krcek Anthony | Combined electric switch and reserve fuse mounting |
| US2313227A (en) * | 1938-08-04 | 1943-03-09 | Metal Carbides Corp | Roll for metal-rolling mills |
| DE941869C (en) * | 1939-05-27 | 1956-04-19 | Eisen & Stahlind Ag | Use of hard metal alloys |
| CH516371A (en) * | 1969-01-02 | 1971-12-15 | Sandco Ltd | Cutting insert for the machining of materials |
| US3609849A (en) * | 1969-04-09 | 1971-10-05 | Jan M Krol | Forming rolls |
| AT327140B (en) * | 1974-05-20 | 1976-01-12 | Plansee Metallwerk | ROLLERS EQUIPPED WITH CARBIDE OR COMPLETE FROM CARBIDE, AND THE PROCESS FOR THEIR PRODUCTION |
| DE2435989C2 (en) * | 1974-07-26 | 1982-06-24 | Fried. Krupp Gmbh, 4300 Essen | Process for the production of a wear-resistant, coated hard metal body for machining purposes |
| JPS5181714A (en) * | 1975-01-14 | 1976-07-17 | Dijet Ind Co Ltd | FUKUGOCHOKOGOKINROORUOYOBI SONOSEIZOHOHO |
| JPS5757525B2 (en) * | 1975-01-23 | 1982-12-04 | Sumitomo Electric Industries | |
| DE2703261B2 (en) * | 1977-01-27 | 1978-11-16 | Roechling-Burbach-Weiterverarbeitung Gmbh, 6620 Voelklingen | Roller body made of hard metal |
| DE2722271C3 (en) * | 1977-05-17 | 1979-12-06 | Thyssen Edelstahlwerke Ag, 4000 Duesseldorf | Process for the production of tools by composite sintering |
-
1979
- 1979-11-23 CA CA000340553A patent/CA1119850A/en not_active Expired
- 1979-11-29 GB GB7941196A patent/GB2036620B/en not_active Expired
- 1979-12-03 JP JP15670279A patent/JPS5594457A/en active Granted
- 1979-12-04 IT IT27852/79A patent/IT1125899B/en active
- 1979-12-04 DE DE2948783A patent/DE2948783C2/en not_active Expired
- 1979-12-04 FR FR7929779A patent/FR2443294A1/en active Granted
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5541006A (en) * | 1994-12-23 | 1996-07-30 | Kennametal Inc. | Method of making composite cermet articles and the articles |
| US5677042A (en) * | 1994-12-23 | 1997-10-14 | Kennametal Inc. | Composite cermet articles and method of making |
| US5679445A (en) * | 1994-12-23 | 1997-10-21 | Kennametal Inc. | Composite cermet articles and method of making |
| US5686119A (en) * | 1994-12-23 | 1997-11-11 | Kennametal Inc. | Composite cermet articles and method of making |
| US5697042A (en) * | 1994-12-23 | 1997-12-09 | Kennametal Inc. | Composite cermet articles and method of making |
| US5697046A (en) * | 1994-12-23 | 1997-12-09 | Kennametal Inc. | Composite cermet articles and method of making |
| US5762843A (en) * | 1994-12-23 | 1998-06-09 | Kennametal Inc. | Method of making composite cermet articles |
| US5789686A (en) * | 1994-12-23 | 1998-08-04 | Kennametal Inc. | Composite cermet articles and method of making |
| US5792403A (en) * | 1994-12-23 | 1998-08-11 | Kennametal Inc. | Method of molding green bodies |
| US5806934A (en) * | 1994-12-23 | 1998-09-15 | Kennametal Inc. | Method of using composite cermet articles |
| US6908688B1 (en) | 2000-08-04 | 2005-06-21 | Kennametal Inc. | Graded composite hardmetals |
Also Published As
| Publication number | Publication date |
|---|---|
| FR2443294B1 (en) | 1983-03-18 |
| GB2036620B (en) | 1983-05-05 |
| IT7927852A0 (en) | 1979-12-04 |
| GB2036620A (en) | 1980-07-02 |
| FR2443294A1 (en) | 1980-07-04 |
| DE2948783C2 (en) | 1986-04-10 |
| JPS5594457A (en) | 1980-07-17 |
| IT1125899B (en) | 1986-05-14 |
| JPS5727162B2 (en) | 1982-06-09 |
| DE2948783A1 (en) | 1980-06-12 |
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