WO2013041559A1 - A roll for hot rolling - Google Patents
A roll for hot rolling Download PDFInfo
- Publication number
- WO2013041559A1 WO2013041559A1 PCT/EP2012/068429 EP2012068429W WO2013041559A1 WO 2013041559 A1 WO2013041559 A1 WO 2013041559A1 EP 2012068429 W EP2012068429 W EP 2012068429W WO 2013041559 A1 WO2013041559 A1 WO 2013041559A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- roll
- high speed
- speed steel
- weight
- hot
- Prior art date
Links
Classifications
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- 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
- B21B27/02—Shape or construction of rolls
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
- B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
-
- 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
- B21B27/02—Shape or construction of rolls
- B21B27/03—Sleeved rolls
- B21B27/032—Rolls for sheets or strips
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/49544—Roller making
Definitions
- the present invention relates generally to the field of rolls for hot-rolling. Furthermore, the present invention relates specifically to the field of work rolls for hot-rolling.
- Hot rolling of metal is a metal forming process that takes place at temperatures above the recrystallization temperature of the metal subjected to forming. This means that the rolling is performed at elevated temperatures, typically at temperatures above 700 ° C. Such high temperature during the rolling operation causes mechanical challenges for the equipment used in hot-rolling. The high temperature causes problems with hardness reduction of the roll material, therefore, the hot hardness of the roll is of utter importance in order to enable longer lifetime of the rolls.
- the rolling sequence In addition to the high temperature, the rolling sequence often comprises cooling of the rolled metal by subjecting the rolls to water, thereby causing large amounts of steam to be formed.
- the steam in combination with elevated temperatures causes severe oxidation of the rolling equipment used and especially the work rolls of the rolling equipment.
- the material used for the rolling rolls therefore needs to withstand high temperature without losing its hardness as well as a good abrasion/wear resistance at said temperatures and atmosphere.
- the work rolls for hot rolling have been manufactured from high chromium nickel cast alloys.
- work rolls for hot-rolling are composite rolls.
- the composite roll comprises a core with suitable mechanical properties, such as ductile iron or steel, and a sleeve with sufficient hot-hardness and sufficient wear resistance for the hot rolling.
- the classical high speed steel exhibits both good hot-hardness and good wear resistance.
- the alloy design of the high speed steel is based on the composition of a so called M2 steel, wherein the main changes being higher carbon and vanadium content.
- a typical composition of such high speed steel often falls into the following ranges: 1 .5-2.5% C, 0-6% W, 0-6% Mo, 3-8% Cr, and 4-10% V.
- the essential target of a rolling mill plant is to keep the shape profile and surface roughness of the rolled metal as close as possible to the target values.
- the better performance of the high speed steel rolls in comparison to the previously used hot roll materials is related to the microstructural characteristics of the high speed steel such as a high amount of very hard and fine MC eutectic carbides and a base matrix hardened by secondary precipitated carbides.
- Roll wear in hot-rolling is a complex process characterized by the concurrent operation of several surface degradation phenomena that involves at least: abrasion, oxidation, adhesion, and thermal fatigue.
- Thermal fatigue stems from stress developed by cyclic heating and cooling of a very thin boundary layer close to the roll surface. Adhesion comes from micro- welding regions of working metal into roll metal in the sticking zone of the roll gap.
- an increase of the volume fraction of eutectic carbides has a beneficial impact on the adhesive behaviour.
- the present invention aims at obviating the aforementioned disadvantages of previously known composite rolls for hot rolling, and also at providing an improved roll for hot-rolling.
- a primary object of the present invention is to provide an envelope surface for a roll for hot rolling with improved wear resistance at elevated temperatures, e.g. above 700 ° C.
- At least the primary object is attained by means of the initially defined roll for hot-rolling having the features defined in the independent claim.
- said sleeve is made of a consolidation of a powder of said high speed steel, which powder is subjected to elevated heat and elevated pressure causing said consolidation.
- the powder is preferably manufactured by argon-atomisation of molten metal comprising said elements into said powder.
- argon-atomisation of the molten metal the amount of nitrides is minimized compared to using nitrogen-atomisation wherein the use of nitrogen gas causes nitrides to form.
- the technical effect of the aforementioned provision of powder is that the rare earth element yttrium is evenly distributed in the powder. If the high speed steel according to the invention would have been produced by a casting method, the highly reactive element yttrium would segregate and not be evenly distributed.
- the carbon (C) content of said high speed steel is in the range of from 1 -3 weight%.
- the amount of carbon should be sufficient to form the carbides necessary for the wear resistance of the high speed steel.
- Preferably the amount of carbon should be enough to produce a high speed steel with sufficient hardenability.
- the higher limit of 3% defines maximum carbon content; above that limit retained austenite may be formed.
- the carbon content is in the range of from 1 .1 -1 .4 weight%.
- the chromium (Cr) content is in the range of 3-6 weight%. This interval causes good hardenability as well as the necessary formation of carbides.
- the Cr content is in the range of from 4.0-5.0 weight%.
- the molybdenum (Mo) content is in the range of 0-7 weight%. Addition of molybdenum causes secondary hardening by precipitation of carbides that will increase the hot hardness and wear resistance of the high speed steel. According to one embodiment, the Mo content is in the range of from 4.5-5.5 weight%.
- the tungsten (W) content is in the range of from 0-15 weight%. Addition of tungsten causes secondary hardening by precipitation of carbides that will increase the hot hardness and wear resistance of the high speed steel. According to an embodiment, the W content is in the range of from 6.0-7.0 weight%.
- the vanadium (V) content is in the range of from 3-14 weight%. Addition of vanadium causes secondary hardening by precipitation of carbides that will increase the hot hardness and wear resistance of the high speed steel. However, too much vanadium causes the high speed steel to become brittle and therefore, the upper limit of 14% should not be exceeded. According to an embodiment, the V content is in the range of from 3.0-5.0 weight%, preferably in the range of from 3.0-3.5 weight%.
- the cobalt (Co) content of said high speed steel is in the range of from 0-10 weight%. Alloying a high speed steel with cobalt improves the tempering resistance and hot hardness, as both are utterly important for a high speed steel to be used in a high temperature wear application.
- the amount of cobalt also has an effect on the hardness of the high speed steel by affecting the amount of retained austenite, causing said retained austenite to be easily converted to martensite during tempering.
- the selected interval for cobalt is a suitable interval for a high speed steel of this composition wherein the upper level is more an economic compromise than a scientific constraint.
- the Co content is 0% or at an impurity level, while according to an alternative embodiment, it is in the range from of 8.0-9.0 weight%.
- the high speed steel should contain yttrium in the interval 0.2% to 1 %, such as from 0.4 to 0.7 weight%, preferably in the range from of 0.45-0.60 weight%, from such as from 0.4 - 0.5 weight%, such as 0.4, 0.41 , 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, and 0.50 weight%.
- the yttrium content defined in the interval above gives the aforementioned positive effects on the oxide scale.
- the yttrium content in the range of from 0.45-0.60 weight% gives a very good increase in the ability of the high speed steel to withstand high temperature wear.
- the lower limit 0.2% of the interval defines a starting point from where a significant positive effect of yttrium on the high temperature wear can be identified, the higher limit of 1 % indicates the end of the interval from where a significant positive effect of yttrium on the high temperature wear can be identified.
- said body comprises an axially extending core, and an axially extending sleeve arranged radially outside said core.
- the core can be constructed to provide excellent heat transfer and mechanical robustness
- the sleeve on the other hand can be arranged to provide excellent wear resistance.
- said sleeve is made of said high speed steel. This causes the wear resistance of said sleeve to exhibit excellent properties for hot rolling, such as wear resistance and hot hardness.
- the powder of which the sleeve is formed is subjected to elevated heat (e.g. 1 150 ° C) and elevated pressure (e.g. 1000 bar) for a long period (e.g. 2 hours), such that a consolidation of the powder is achieved.
- the sleeve of consolidated powder is then subjected to a soft annealing step at 900 ° C followed by a temperature decrease to 700 ° C at a cooling rate of 10 ° C/hour, from thereon the sleeve is allowed to naturally cool down to room temperature.
- This soft annealing step causes the carbides in the high speed steel to spheroidize.
- the sleeve is thereafter preferably subjected to machining and thereafter heat treated with a hardening (austenizing) step at 1 100 ° C and three subsequent annealing steps at 560 ° C for 60 minutes each, with natural cooling to room temperature there between.
- said core is made of cast steel or forged steel.
- a core made of cast steel or cast iron or forged steel is easy to machine and heat treat to the desired functionality.
- Such a core is also cost effective and easy to produce.
- the microstructure of the sleeve is isotropic. As a result thereof, the wear properties of the sleeve material are improved.
- the material of said sleeve contains carbide particles that have a mean carbide particle size which is ⁇ 3 ⁇ .
- said sleeve is shrink fitted onto said core.
- Figure 1 is a perspective view of a compound roll
- Figure 2 is a schematic figure of a "pin on disc” test equipment
- Figure 3 shows a cross section of a typical groove obtained from a "pin on disc” evaluation, perpendicular to the longitudinal direction
- Figure 4 is a diagram showing the groove depth at room temperature and 650 ° C for the alloys A, B and C in the "pin on disc” experiment,
- Figure 5 is a diagram showing the volume loss per meter at 650 ° C for the alloys A, B and C in the "pin on disc” experiment.
- Figure 6 shows the hardness in HRC for alloy A, B and C.
- the industrial production of semi-finished products, components and cutting tools based on powder metallurgical high speed steel started 35 years ago.
- the first powder metallurgical production of high speed steel was based on hot isostatic pressing (HIP) and consolidation of atomized powders.
- the HIP step was normally followed by hot forging of the HIP'ed billets. This method of production is still the dominating powder metallurgical method to produce high speed steel.
- the original objective for research and development on powder metallurgical processing of high speed steel was to improve the functional properties and performance of high speed steel in demanding applications.
- the main advantages from the powder metallurgical manufacturing process are no segregation with a uniform and isotropic microstructure.
- the well known problems with coarse and severe carbide segregation in conventional cast steel and forged steel are thus avoided in powder metallurgical high speed steel.
- the powder metallurgical manufacturing method of a high speed steel with sufficient amount of carbon and carbide forming elements results in a dispersed distribution of carbides that to a large extent solves the problem of low strength and toughness associated with conventionally produced high speed steel.
- FIG. 1 shows a composite roll 101 for hot-rolling.
- the roll 101 comprises an axially extending core 102 with an envelope surface 104 formed by an axially extending sleeve 103 arranged radially outside said core 102.
- the core 102 is manufactured of a material with good mechanical properties and good heat conductive properties, examples of such materials are ductile iron or steel.
- the core 102 is a cylindrical journal that comprises at a first end and at a second end means for support bearings. The support bearings allow the working roll to be mounted in the hot rolling mill. Between said first end and said second end is provided a longitudinal region arranged for shrink fitting of the sleeve 103 onto said core 102.
- the sleeve 103 is a cylindrical sleeve with an inner diameter that is dimensioned for shrink fitting the sleeve 103 onto said core 102.
- the wall thickness of the sleeve 103 is
- the sleeve 103 is made of a high speed steel that with reference to its chemical composition consists of the following elements: 1 -3 wt-% Carbon (C), 3-6 wt-% Chromium (Cr), 0-7 wt-% Molybdenum (Mo), 0-15 wt-% Tungsten (W), 3-14 wt- % Vanadium (V), 0-10 wt-% Cobalt (Co), 0-3 wt-% Niobium (Nb), 0-0.5 wt-% Nitrogen (N), 0.2-1 wt-% Yttrium (Y), and remainder iron (Fe) and unavoidable impurities.
- the manufacturing of the sleeve 103 comprises of a powder of said high speed steel to form a body from said powder.
- This forming may for example comprise pouring said powder into a capsule in the form of the sleeve 103; the capsule is then evacuated and sealed.
- the capsule is subjected to heat and pressure in a so called hot isostatic processing (HIP) step.
- HIP hot isostatic processing
- the provision of the powder mixture comprises the step of argon gas-atomisation of molten metal comprising said elements into said powder.
- the argon gas-atomisation of the molten high speed steel causes high speed steel particles of a maximum size of 160 ⁇ to be formed.
- the sleeve is formed from said powder.
- This forming may for example comprise pouring said powder into a capsule; the capsule is then evacuated, e.g. by being subjected to a pressure of below 0.004 mbar for 24 hours in order to evacuate said capsule. The capsule is then sealed in order to maintain said pressure in the capsule.
- the consolidation of the powder is achieved by subjecting the capsule to an elevated temperature, e.g. about 1 150 ° C, and an elevated pressure, e.g. about 1000 bar, for a long period of time, e.g. two hours. This last consolidation step is called hot isostatic pressing, HIP.
- a soft annealing step follows the HIP step, preferably the soft annealing step is performed at 900 ° C followed by a temperature decrease to 700 ° C at a cooling rate of 10 ° C/hour, from thereon the sleeve is allowed to naturally cool down to room temperature.
- the sleeve may be subjected to machining and preferably a hardening (austenizing) step at 1 100 ° C and three subsequent annealing steps at 560 ° C for 60 minutes each, with natural cooling to room temperature there between.
- the resulting sleeve from these subsequent steps exhibits a very good uniformity without the aforementioned segregations and coarse carbide structure, and the most important effect is that the yttrium element is evenly distributed in the base-matrix of the high speed steel.
- Table 1 shows the elements of the high speed steel used in the experiment. Smelts were produced with the elements in table 1 , and from these smelts, powders were produced be means of gas atomisation using argon.
- the powders of alloy B and C in table 1 have a particle size of ⁇ 160 ⁇ , the powder of alloy A has a particle size of ⁇ 500 ⁇ .
- the preparation of samples began with filling of the capsules with powder, with said capsules made from spiral welded tubes with a diameter of 73 mm. The capsules were then exposed to a pressure below 0.004 mbar for 24 hours. The capsules were then sealed in order to maintain said pressure.
- a hot isostatic pressing operation was performed at 1 150 ° C and 1000 bar for 2 hours.
- the samples were then subjected to a soft annealing step at 900 ° C followed by a temperature decrease to 700 ° C at a cooling rate of 10 ° C/hour, from thereon the samples were allowed to naturally cool down to room temperature.
- the samples were then machined and heat treated with a hardening (austenizing) step at 1 100 ° C and three subsequent annealing steps at 560 ° C for 60 minutes each, with natural cooling to room temperature there between.
- a hardening (austenizing) step at 1 100 ° C and three subsequent annealing steps at 560 ° C for 60 minutes each, with natural cooling to room temperature there between.
- the final preparation step comprised of stepwise grinding and polishing of the samples in an automatic grinder/polisher. During the final polishing step a 1 ⁇ diamond suspension was used.
- Figure 2 shows a simplified test set-up used for the tribological testing; this set-up is in the art called "pin on disc".
- the principle for the "pin on disc” tribological testing is as follows; a sample 1 is rotated around an axis 5 with a speed ⁇ for a number of revolutions.
- a force F is applied to a pin 2 that in turn applies the same force F to a ball 3.
- the ball 3 is made of Al 2 0 3 and has a diameter of 6 mm.
- the rotation of the sample 1 and the force F on the ball 3 causes a groove 6 to be formed in the sample 1 .
- the lower part of the "pin on disc" set-up is accommodated in a furnace 4.
- the furnace 4 can heat the sample 1 , the ball 3 and the lower part of the pin 2 to the desired operating temperature.
- Figure 3 shows a cross section of the groove 6 perpendicular to the longitudinal direction of the groove 6.
- the depth d measured from the polished surface of the sample to the bottom of the groove 6 is used as a measure of the wear resistance of the sample.
- Another figure of the wear resistance is the cross-sectional area 7, which is defined as the cross-sectional area of the groove 6 below the polished surface of the sample 1 perpendicular to the longitudinal direction of the groove 6.
- the profile and depth d of the groove 6 was estimated using a Veeco Wyko NT9100 white light interferometer.
- volume loss per meter is presented; volume loss for alloy A is 4.6x 1 0 "5 mm 3 /m, volume loss for alloy B is 1 .8x 1 0 "5 mm 3 /m and finally the volume loss for alloy C is 4x 1 0 ⁇ 5 mm 3 /m.
- the relationship between the yttrium content of the high speed steel and the volume loss per meter thereof is illustrated in figure 5. From figure 5 one can conclude that the yttrium content of 0.5 % clearly results in the lowest volume loss per meter. A higher yttrium content than 1 % also has a beneficial effect on the volume loss per meter.
- the yttrium content of the high speed steel is within the range 0.2 to 1 weight%. It is preferred that the yttrium content of the high speed steel is more than 0.4 weight%, and less than 0.7 weight, more preferably 0.4 to 0.6 weight%, such as 0.4 to 0.5 weight%, such as 0.4, 0.41 , 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, 0.49 and 0.5.
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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Abstract
Description
Claims
Priority Applications (9)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
BR112014006532A BR112014006532A2 (en) | 2011-09-19 | 2012-09-19 | hot rolling roll |
KR1020147009616A KR101988685B1 (en) | 2011-09-19 | 2012-09-19 | A roll for hot rolling |
RU2014115715A RU2609115C2 (en) | 2011-09-19 | 2012-09-19 | Roll for hot rolling |
MX2014003248A MX367214B (en) | 2011-09-19 | 2012-09-19 | A roll for hot rolling. |
EP12759475.2A EP2758559B1 (en) | 2011-09-19 | 2012-09-19 | A roll for hot rolling |
JP2014531205A JP6016927B2 (en) | 2011-09-19 | 2012-09-19 | Hot rolling roll |
US14/345,443 US9993858B2 (en) | 2011-09-19 | 2012-09-19 | Roll for hot rolling |
UAA201404172A UA111505C2 (en) | 2011-09-19 | 2012-09-19 | Roll for hot rolling |
CN201280045622.5A CN103814147A (en) | 2011-09-19 | 2012-09-19 | A roll for hot rolling |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP11181778.9 | 2011-09-19 | ||
EP11181778A EP2570508A1 (en) | 2011-09-19 | 2011-09-19 | A roll for hot rolling |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013041559A1 true WO2013041559A1 (en) | 2013-03-28 |
Family
ID=46852028
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/EP2012/068429 WO2013041559A1 (en) | 2011-09-19 | 2012-09-19 | A roll for hot rolling |
Country Status (10)
Country | Link |
---|---|
US (1) | US9993858B2 (en) |
EP (2) | EP2570508A1 (en) |
JP (1) | JP6016927B2 (en) |
KR (1) | KR101988685B1 (en) |
CN (2) | CN103814147A (en) |
BR (1) | BR112014006532A2 (en) |
MX (1) | MX367214B (en) |
RU (1) | RU2609115C2 (en) |
UA (1) | UA111505C2 (en) |
WO (1) | WO2013041559A1 (en) |
Cited By (1)
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DE102014000165A1 (en) * | 2014-01-07 | 2015-07-09 | Horst Diesing | Alloy and process for matrix intrinsic tribocharged manganese oxide coatings for increased service life of hot working tools from S (HSS) iron base alloys |
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CN109825773B (en) * | 2019-04-10 | 2020-07-10 | 安徽环渤湾高速钢轧辊有限公司 | Thick-wall high-speed steel wear-resistant roll collar and preparation method thereof |
CN111647812A (en) * | 2020-05-31 | 2020-09-11 | 河冶科技股份有限公司 | Special steel for rolling roller blank and preparation method thereof |
CN112941402A (en) * | 2021-01-28 | 2021-06-11 | 黄石中睿科技有限责任公司 | Wear-resistant alloy bar and preparation method thereof |
CN114713796B (en) * | 2022-05-06 | 2024-04-19 | 湖南三泰新材料股份有限公司 | Hot-rolled powder high-speed steel and preparation method thereof |
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- 2012-09-19 KR KR1020147009616A patent/KR101988685B1/en active IP Right Grant
- 2012-09-19 JP JP2014531205A patent/JP6016927B2/en not_active Expired - Fee Related
- 2012-09-19 WO PCT/EP2012/068429 patent/WO2013041559A1/en active Application Filing
- 2012-09-19 MX MX2014003248A patent/MX367214B/en active IP Right Grant
- 2012-09-19 CN CN201280045622.5A patent/CN103814147A/en active Pending
- 2012-09-19 UA UAA201404172A patent/UA111505C2/en unknown
- 2012-09-19 US US14/345,443 patent/US9993858B2/en not_active Expired - Fee Related
- 2012-09-19 CN CN201810467190.6A patent/CN108642401A/en active Pending
- 2012-09-19 RU RU2014115715A patent/RU2609115C2/en not_active IP Right Cessation
- 2012-09-19 BR BR112014006532A patent/BR112014006532A2/en not_active IP Right Cessation
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DE102014000165A1 (en) * | 2014-01-07 | 2015-07-09 | Horst Diesing | Alloy and process for matrix intrinsic tribocharged manganese oxide coatings for increased service life of hot working tools from S (HSS) iron base alloys |
DE102014000165B4 (en) * | 2014-01-07 | 2016-06-09 | Horst Diesing | Alloy for matrix intrinsic tribocharged manganese oxide coatings for extended service life of hot working tools made from S (HSS) iron based alloys |
Also Published As
Publication number | Publication date |
---|---|
EP2570508A1 (en) | 2013-03-20 |
EP2758559B1 (en) | 2019-08-28 |
JP2014531982A (en) | 2014-12-04 |
RU2609115C2 (en) | 2017-01-30 |
US20150018185A1 (en) | 2015-01-15 |
JP6016927B2 (en) | 2016-10-26 |
EP2758559A1 (en) | 2014-07-30 |
CN108642401A (en) | 2018-10-12 |
KR20140064953A (en) | 2014-05-28 |
CN103814147A (en) | 2014-05-21 |
KR101988685B1 (en) | 2019-06-12 |
RU2014115715A (en) | 2015-10-27 |
US9993858B2 (en) | 2018-06-12 |
MX2014003248A (en) | 2014-04-10 |
BR112014006532A2 (en) | 2017-04-04 |
UA111505C2 (en) | 2016-05-10 |
MX367214B (en) | 2019-08-09 |
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