CN103108975A - A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll - Google Patents
A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll Download PDFInfo
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- CN103108975A CN103108975A CN2011800001367A CN201180000136A CN103108975A CN 103108975 A CN103108975 A CN 103108975A CN 2011800001367 A CN2011800001367 A CN 2011800001367A CN 201180000136 A CN201180000136 A CN 201180000136A CN 103108975 A CN103108975 A CN 103108975A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K1/00—Making machine elements
- B21K1/02—Making machine elements balls, rolls, or rollers, e.g. for bearings
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/06—Surface hardening
- C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
- C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- 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
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
This invention relates in general to the field of forged rolls and to production of forged rolls. More particularly the present invention relates to forged rolls for use in the cold rolling industry. The present invention relates to a forged roll for use in the cold rolling industry and a method for production of such a roll. Said forged roll, comprises a steel composition and a microstructure that comprises: - tempered martensite with a retained austenite rate less than (<) 5 % per volume; and - an open eutectic carbide network with eutectic carbides of less than (<) 5 % per volume; and wherein the roll exhibits: - a hardness between 780-840HV; and - internal compressive between -300 to -500 MPa in absolute values.
Description
Technical field
The present invention relates in general to the field of forged roll and the production of forged roll.More specifically, the forged roll that the present invention relates to satisfy the demand of cold rolling industry and be mainly used in cold rolling industry.
Background technology
General background
The general trend of the cold rolling development of iron and non-ferrous metal industry is rolling faster, thinner and wider.Current challenge is to complete above-mentioned trend in planeness, thickness and the appearance of realizing perfect control and high productivity compatibility.Therefore, this trend requires to use the advanced rolling technique of controlling crucial rolling parameter.
Some key parameters such as roughness confining force and appearance can be guaranteed by the chromium plating working roll.This measure is effective and efficient, but just becoming due to environmental restraint, problem is arranged more and more, and it is unacceptable to become in the near future.
At present, (2～6%Cr) are generally used for cold-rolling process to the working roll of chrome faced forging.It is in order to improve wear resistance with regard to the surface tissue confining force that this roller is carried out chromium plating, itself so that will guarantee the higher gloss of making peace after japanning of car body for example.Hard electrolytic deposition technology as chromium plating is developed for tempering/skin-pass (skin pass) milling train uses at first.In these were used, the chromium plating working roll presented the life-span than long 2～8 times of nothing coating roller, was mainly due to better roughness confining force.The enforcement of this technology extends to attenuate milling train (reduction mill) gradually.
In addition, also exist the intention made by rapid steel (HSS) without the forged roll that uses under coating state, but need the low roller of residualinternal stress, and need to produce the industrial technology of this roller, its intention is used for milling train when giving to be equivalent at least to have the roughness confining force of coating roller under uncoated state.
Concrete background
Produce the roller that uses in the industry at Cold-roller management processing conditioned disjunction concrete operations stress during use, be easy to explode in order to do not crack or become.The blast of roller can relate to collateral damage in operator's safety and milling train.Therefore, need the low roller of residualinternal stress.
Prior art
Disclose towards the example that develops without the coated high speed steel roller with the prior art that is used for cold rolling purpose:
C.Gaspard，C.Vergne，D.Batazzi，T.Nylen，P.H.Bolt，S.Mul，K.M.Reuver：″Implementation?of?in-service?key?parameters?of?HSS?work?roll?grade?dedicated?to?advanced?cold?rolling″，IST?Conference?May?3-6，2010，Pittsburgh，Pa，USA
C.Gaspard，S.Bataille，D.Batazzi，P.Thonus：″Improvement?For?Advanced?Cold?Rolling?Reduction?Mills?By?Using?Semi-HSS?and?HSS?Rolls″，7th?International?Conference?on?Steel?Rolling(ISIJ)，Makuhari，Chiba，Japan，1998
P.H.Bolt，D.Batazzi，N.P.Belfiore，C.Gaspard，L.Goiset，M.Laugier，O.Lemaire，D.Matthews，T.Nylén，K.Reuver，D.Stocchi，F.Stork，J.Tensen，M.Tornicelli，R.Valle，E.van?den?Elzen，C.Vergne，I.M.Williams：″Damage?Resistance?and?Roughness?Retention?of?work?Rolls?in?cold?Rolling?Mills″，5th?European?Rolling?Conference，23-25?June?2009，London，UK
Other examples of prior art appear in following patent publications: JP09003603, JP53077821, JP57047849, JP2002285284, JP2002285285, JP10317102, JP1208437, EP0395477 and JP08158018, they have described the cold rolling working roll of using that is used for strengthening wearing and tearing and scaling resistance.
Yet these prior aries are not open to be realized and can make under the condition of this high speed steel rider in cold-rolling mill operating necessary parameter and character.
Summary of the invention
Purpose of the present invention
Overall purpose
Overall purpose of the present invention be to provide a kind of can the condition in cold-rolling mill under preferred roller and production technique thereof to operate without coating form.More specifically purpose is to provide a kind of roller and production technique thereof, keep simultaneously with prior art, the suitable tribological properties such as low-friction coefficient, high roughness confining force, iron powder dust pollution of coating roller being arranged at least, and compare with known roller, in operation than the rolling mill characteristic that presents improvement with regard to high cracking resistance and higher-security.
Subproblem
The present invention further seeks to solve following subproblem:
-improve roll surface, give roller higher performance
-avoid roller scaling accident
-avoid the roller production technique of not environmental protection
-improve rolling distance or the life-span of roller, allow the longer running of each milling train operation.
Summary of the invention
The solution of the problem of more than enumerating, subproblem and aspect is according to a kind of roller of the present invention, and what it had an improvement adds thermal crack drag and low crack propagation power, to reduce the susceptibility to the milling train accident when keeping than high-wearing feature.
A kind of method that the invention provides forged roll for cold rolling industry and produce this roller.This roller still also can have coating preferably without coating.
A first aspect of the present invention relates to a kind of forged roll, and it comprises a kind of composition of steel, and this composition of steel comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
The microstructure of wherein said roller comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And wherein said roller presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
In other embodiment of the present invention, roller of the present invention comprises the open eutectic carbides net of the eutectic cell that defines colony shape apperance.
Other modification of roller comprises any one of following aspect optional, independent or capable of being combined:
A kind of roller, the open eutectic carbides net of wherein said roller comprises dendritic arm (dendritic arm).
A kind of roller, the open eutectic carbides net form of wherein said roller becomes a plurality of eutectic carbides mesh portions of substantial separation.
A kind of roller, the microstructure of wherein said roller is present in the working lining of roller at least.
A kind of roller has the following composition of steel of component with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
Ni less than (＜) 1%
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2
Less than the W of (＜) 2%, and
Less than the Nb of (＜) 1%, and
Less than the Ti of (＜) 1%, and
Less than the Ta of (＜) 0.5%, and
Less than the Zr of (＜) 0.5%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
According to roller of the present invention, wherein the C content in composition of steel account for regard to weight percent whole roller heavy 0.8～0.99%.
According to roller of the present invention, wherein the C content in composition of steel account for regard to weight percent whole roller heavy 0.85～0.9%.
According to roller of the present invention, wherein the Mn content in composition of steel account for regard to weight percent whole roller heavy 0.4～0.5%.
According to roller of the present invention, wherein the Si content in composition of steel account for regard to weight percent whole roller heavy 0.2～1.5%.
According to roller of the present invention, wherein the Si content in composition of steel account for regard to weight percent whole roller heavy 0.85～1.15%.
According to roller of the present invention, wherein the Cr content in composition of steel account for regard to weight percent whole roller heavy 7.0～11%.
According to roller of the present invention, wherein the Cr content in composition of steel account for regard to weight percent whole roller heavy 7.3～less than (＜) 8.0%.
According to roller of the present invention, wherein the Mo content in composition of steel account for regard to weight percent whole roller heavy 1.45～1.55%.
According to roller of the present invention, wherein the Ni content in composition of steel account for regard to weight percent whole roller heavy less than (＜) 0.3.
According to roller of the present invention, wherein the V content in composition of steel account for regard to weight percent whole roller heavy 1.3～2.1%.
According to roller of the present invention, wherein the V content in composition of steel account for regard to weight percent whole roller heavy 1.3～1.6%.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
0.8～0.99% C, and
0.4～0.5% Mn, and
0.2～1.5% Si, and
7.0～11% Cr, and
0.6～1.6% Mo, and
Less than the Ni of (＜) 1.0, and
1.0～2.1% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
0.85～0.9% C, and
0.4～0.5% Mn, and
0.85～1.15% Si, and
7.3～less than the Cr of (＜) 8.0%, and
1.45～1.55% Mo, and
Less than the Ni of (＜) 0.3, and
1.3～1.6% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
Roller of the present invention further is structured as the working roll in cold rolling.
Roller of the present invention further has the weight greater than 400kg.
Roller of the present invention further has the diameter of 215～800mm scope.
Another aspect of the present invention provides the forged roll that generates by the technique that comprises the following steps:
A., a kind of composition of steel is provided, and it comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity; In further embodiments, composition of the present invention is as described in any one of above-mentioned composition or composition combination;
B. make ingot casting, keep the solidification rate higher than 15 ℃/min in the freezing range in the upper layer (upper layer that is equivalent to roller) of ingot casting;
C. this ingot casting is forged into roller;
D. make the roller sclerosis by induction heating;
E. pair roller carries out tempering;
Thereby obtain the microstructure of described roller, it comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And wherein said roller (1) presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
Other modification of roller comprises any one about the aspect following optional, independent or capable of being combined of the chemical composition of above-mentioned roller or microstructure, and comprises the feature of any one of following optional, independent or aspect capable of being combined.
Another aspect of the present invention provides a kind of technique for the manufacture of non-forged roll of the present invention, and this technique comprises the following steps:
A., a kind of composition of steel is provided, and it comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity; In further embodiments, composition of the present invention is as described in any one of above-mentioned composition combination;
B. make ingot casting, keep the solidification rate higher than 15 ℃/min in the freezing range in the working lining (working lining that is equivalent to roller) of ingot casting;
C. this ingot casting is forged into roller;
D. make the roller sclerosis by induction heating;
E. with the temperature of 450～530 ℃, described roller is carried out tempering to reach the hardness of 780～840HV;
Thereby obtain the microstructure of described roller (1), it comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And wherein said roller (1) presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
Other modification of roller comprises any one of following aspect optional, independent or capable of being combined.
According to technique of the present invention, wherein, the solidification rate of working lining and core is maintained 15 ℃/min～55 ℃/min or 17 ℃/min～50 ℃/min or 35 ℃/min～55 ℃/min or 45 ℃/min～55 ℃/min, make ingot casting.
According to technique of the present invention, wherein, keep the solidification rate higher than 35 ℃/min in the freezing range in the working lining of ingot casting or surface, make ingot casting.
According to technique of the present invention, wherein, for described ingot casting, described freezing range is 1400～1200 ℃.
According to technique of the present invention, wherein, control ampere electric current source (ampere current supply) according to the predefined function (function) of solidification rate, thereby keep the solidification rate of selecting in advance in the electroflux refining furnace technical matters, make ingot casting.
A kind of technique, the step that wherein ingot casting is forged into roller comprises the following steps:
A. ingot casting is heated to approximately 850～1100 ℃ or 800～1000 ℃, preferably continues approximately 6 hours;
B. higher than approximately 800 ℃ or forge described ingot casting higher than the temperature of 850 ℃;
C. repeating step a～b is until described ingot casting forms the roller with intended shape and size.
A kind of technique also comprises the preliminary heat treated step that roller stock is applied after forging step, preferably to the about temperature of 700～1100 ℃ or 800～900 ℃, can comprise the hydrogen DIFFUSION TREATMENT.
A kind of technique also comprises by progressive induction heating carries out case-hardened step, preferably in the about temperature of 900～1150 ℃.
A kind of technique, wherein the pair roller step of carrying out tempering comprises the following steps:
D. heat described roller to approximately 450～530 ℃ or 450～520 ℃, preferred 3 times,
E. between each heating steps, described roller is carried out air cooling.
A kind of technique also comprises described roller is carried out mechanical workout, comprises the white layer of eutectic carbides with processing (texturing).
Other modification of technique of the present invention comprises any one about the aspect following optional, independent or capable of being combined of the chemical composition of above-mentioned roller or microstructure, and comprises the feature of any one of following optional, independent or aspect capable of being combined.
Another aspect of the present invention provides the intermediates ingot casting in a kind of production process of roller, and this ingot casting comprises a kind of composition of steel, and this composition of steel comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
And the microstructure of the final roller of wherein making from described ingot casting comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent.
In the middle of of the present invention, other modification of ingot casting comprises any one about the aspect following optional, independent or capable of being combined of the chemical composition of above-mentioned ingot casting, and comprises the feature of any one of following optional, independent or aspect capable of being combined.
Another aspect of the present invention provides a kind of purposes of forged roll of the present invention, is used for the material of the high rolling load of cold rolling demand.
Other embodiment of the present invention provide a kind of purposes of forged roll, are used for cold rolling such as high-strength materials such as AHSS grades of steel.
According to the purposes of forged roll of the present invention, be used for following option:
-be used for the cold rolling attenuate milling train of reversible and irreversible frame, roughing and the finishing stand of tin plate, sheet material, silicon steel, stainless steel, aluminium and copper; Or
-cold rolling tempering and/or skin-pass milling train; Or
-be configured to have and processed or the undressed milling train of two rollers, four rollers and six roller frames on surface excessively.
The working roll that is used as according to forged roll of the present invention.
Roller of the present invention is fitted in many application and is used as without coating roller.Yet aspect other and in embodiment, roller also can be provided with coating of the present invention, selects to be used for current or specific application arbitrarily.Coating can be chromiumcoating for example.Roller also can be used for warm-rolling and uses.
Description of drawings
The below will further describe the present invention by some embodiment of illustration, wherein:
Fig. 1 is the schematic diagram of roller of the present invention.
Fig. 2 is the schematic diagram of roller production technique of the present invention.
Fig. 3 is the schematic diagram of ingot casting of the present invention.
Fig. 4 shows the manufacturing process of ingot casting of the present invention.
Fig. 5 A～5B shows the cast microstructure of using the roller trade mark that production technique of the present invention makes.This roller trade mark is with shown in the sectional view of its working lining.
Fig. 6 A～6B shows the cast microstructure of using the roller trade mark that production technique of the present invention makes.This roller trade mark is with shown in the sectional view of its working lining.
But Fig. 7 A～7C shows and uses production technique difference of the present invention is to use the cast microstructure of the roller trade mark that too low solidification rate makes.This roller trade mark is with shown in the sectional view of its working lining.
Fig. 8 shows first group of example of the solidification rate of roller production technique of the present invention.
Fig. 9 shows second group of example of the solidification rate of roller production technique of the present invention.
Figure 10 A～10B shows the cast microstructure of the ingot casting of making when using production technique of the present invention under laboratory condition.
The cast microstructure of the ingot casting that Figure 11 A～11B makes under laboratory condition when showing the Mo too high levels of using production technique of the present invention but using.
Figure 12 is the schematic diagram that forges according to the present invention.
Figure 13 A～13C is the schematic diagram that ingot casting is formed the step of roller of the present invention by forging.
Figure 14 carries out the schematic diagram of progressive induction hardening to roller of the present invention with different frequency.
Figure 15 A～15B shows the microstructure on the surface of roller after surface working (electric discharge surface processing) of standard brand.
Figure 15 C～15D shows the microstructure on the surface of roller of the present invention after surface working (electric discharge surface processing).
Figure 16 A～16D shows the injurous defect of the roller that generates when making roller with low chromium content and high molybdenum content.
Figure 17 A shows an example of the microstructure of the present invention with open eutectic net.
Figure 17 B shows the example of the microstructure with sealing eutectic net, and wherein eutectic carbides 200 forms the sealing eutectic net that eutectic cell 212 obviously separates.
Figure 18 shows the example of the microstructure of surface after electric discharge surface processing of roller of the present invention.
Figure 19 A～19B shows place that on roll surface, 4mm is dark in the tempering of roller and the roller microstructure after induction hardening.
Embodiment
Introduce
The present invention relate in general to that weight is preferably greater than 400kg or as being used for the embodiment of common application weight greater than the forged roll 1 of 1000kg.Roller of the present invention is to be known according to general step itself but specifically to adapt to into according to the innovation concept the forged roll production method that can produce roller of the present invention and generate.
The present invention relates generally to the roller that weight is 400kg～10000kg.The diameter 2 of roller of the present invention be for example 215～800mm, and the length of its cylindrical shell 8 is generally 1～3 meter, and comprises that the maximum length of neck 10 is generally approximately 6 meters generally greater than 200mm.Roller 1 has working lining 4, and it is corresponding to an outer field part, and general diameter is 20mm～120mm, depends on the application of concrete roller and/or depends on whole roller diameter 2.Usually, the outside 1/6 part 6 of the diameter 2 of roller is called the working lining 4 of roller 1, sees Fig. 1.In this article, the outside 1/6 part 6 of the diameter 2 of ingot casting 34 is also referred to as the working lining 4 of ingot casting 34.
There are special problem and challenge when making large forged roll, because the internal stress that relates to when forming these large roller.The roller that diameter is less does not need identical processing, because the internal stress of this moment is lower, and these rollers are for example not easy to explode between hardening period.
12 pairs of rollers 1 of making size of the present invention of roller production technique of the present invention are most important.Obtained the mechanical property such as improvement such as low residualinternal stresses of roller of the present invention by roller production technique 12.For the level of the residualinternal stress that makes the gained roller is low, the internal stress that must thermal gradient and polymorphic transformation be caused in all stages of the production technique by casting, forging, thermal treatment and mechanical workout minimizes.The microstructure of roller 1 of the present invention comprises that because of the production technique of chemical composition of the present invention and roller the residual ratio of austenite is lower than the tempered martensite of 5% volume percent.
Roller production technique of the present invention comprise following in the schema of Fig. 2 the selected works (selection) of schematically illustrated basic step:
14. a kind of composition of steel is provided
16. make ingot casting 34
18. described ingot casting 34 is forged into roller 1
20. described roller 1 is carried out preliminary thermal treatment
22. the described roller 1 of roughing
24. the described roller 1 of induction hardening
26. described roller 1 is carried out tempering heat treatment
28. process described roller 1
Obtain intermediates after each step.Select the concrete chemical composition of controlling parameter and roller to produce roller of the present invention.
The roller production technique
The present invention relates to the forged roll 1 by the technique generation that comprises the following steps:
A., a kind of composition of steel is provided, and it comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
B. make ingot casting, keep the solidification rate higher than 15 ℃/min in the working lining of freezing range (interval) at ingot casting;
C. this ingot casting is forged into roller;
D. make the roller sclerosis by induction heating;
E. pair roller carries out tempering;
Thereby obtain the microstructure of roller 1, it comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And its central roll 1 presents:
-greater than the hardness of 780HV; With
-absolute value is less than the internal compression stresses of-500MPa.
The chemical composition of the present invention with combination of process steps use of the present invention that wherein provides gives the performance of roller of the present invention with expectation in the microstructure of roller of the present invention.
The manufacturing process of forged roll of the present invention comprises the following steps:
Step 14: a kind of composition of steel is provided.
In one embodiment of the invention, described composition of steel comprises the alloy that following component as expressed in weight percent formed or consisted of as enumerating in table 1.The effect of the roller of the present invention that in table 1, the impact of component has been described, obtains by the component selected and concrete interval.
Table 1
And comprise also that alternatively content is separately lower than the H of 0.4% (weight)
2, N
2, O
2, Al, Cu; And wherein the inevitable impurity of the remainder eliminating minute element of composition of steel and possibility be mainly Fe outward.
In an embodiment of the present invention, composition of steel comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
Wherein the inevitable impurity of the remainder eliminating minute element of steel and possibility be mainly Fe outward.
In different embodiments of the invention and modified example, composition comprises or construct is combination or selected works according to the component (% by weight) of following example.In some cases, previous embodiment and following group component modified example make up, are replaced or narrow down by following group component modified example.
A kind of roller has the following composition of steel of component with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
Ni less than (＜) 1%
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H2 less than (＜) 3ppm
Less than the W of (＜) 2%, and
Less than the Nb of (＜) 1%, and
Less than the Ti of (＜) 1%, and
Less than the Ta of (＜) 0.5%, and
Less than the Zr of (＜) 0.5%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity.
According to roller of the present invention, wherein the C content in composition of steel account for regard to weight percent whole roller heavy 0.8～0.99%.
According to roller of the present invention, wherein the C content in composition of steel account for regard to weight percent whole roller heavy 0.85～0.9%.
According to roller of the present invention, wherein the Mn content in composition of steel account for regard to weight percent whole roller heavy 0.4～0.5%.
According to roller of the present invention, wherein the Si content in composition of steel account for regard to weight percent whole roller heavy 0.2～1.5%.
According to roller of the present invention, wherein the Si content in composition of steel account for regard to weight percent whole roller heavy 0.85～1.15%.
According to roller of the present invention, wherein the Cr content in composition of steel account for regard to weight percent whole roller heavy 7.0～11%.
According to roller of the present invention, wherein the Cr content in composition of steel account for regard to weight percent whole roller heavy 7.3～less than (＜) 8.0%.
According to roller of the present invention, wherein the Mo content in composition of steel account for regard to weight percent whole roller heavy 1.45～1.55%.
According to roller of the present invention, wherein the Ni content in composition of steel account for regard to weight percent whole roller heavy less than (＜) 0.3.
According to roller of the present invention, wherein the V content in composition of steel account for regard to weight percent whole roller heavy 1.3～2.1%.
According to roller of the present invention, wherein the V content in composition of steel account for regard to weight percent whole roller heavy 1.3～1.6%.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
0.8～0.99% C, and
0.4～0.5% Mn, and
0.2～1.5% Si, and
7.0～11% Cr, and
0.6～1.6% Mo, and
Less than the Ni of (＜) 1.0, and
1.0～2.1% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
0.85～0.9% C, and
0.4～0.5% Mn, and
0.85～1.15% Si, and
7.3～less than the Cr of (＜) 8.0%, and
1.45～1.55% Mo, and
Less than the Ni of (＜) 0.3, and
1.3～1.6% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
Step 16: the manufacturing step 16 of cylindrical ingot casting 34
In typically used of the present invention, a kind of intermediates be the ingot casting 34 that the method according to this invention generates preferably have the diameter 32 of 450～1100mm, up to the weight of the length of 6 meters 30 and 400～30000kg, see Fig. 3.The manufacture method of ingot casting 34 of the present invention relates to during the manufacturing of ingot casting 34 the quick cooling technology that can realize of using.For example, ingot casting 34 can generate by different ingot casting formation technology.Suitable manufacturing technology is can be controlled to obtain and to keep the technology of specific minimum solidification rate.
According to embodiments of the invention, during forming ingot casting, average solidification rate is controlled to be on the surface higher than 15 ℃/min, and at core preferably also higher than 10 ℃/min.Preferably, when cooling ingot casting material is controlled in the freezing range that for example can be 1400 ℃～1200 ℃, keep this solidification rate.In other embodiment of the present invention, in this freezing range, in working lining, average solidification rate is controlled to be higher than 35 ℃/min.
From practical point of view, generally be difficult to obtain very high solidification rate when enforcement is of the present invention.Some embodiment more of the present invention are included in and in working lining and core, average solidification rate are controlled to be 15 ℃/min～55 ℃/min or 35 ℃/min～55 ℃/min or 45 ℃/min～55 ℃/min.
The technology that is used in the present invention the control technique relevant with Solidification Parameters of the present invention is for example dissimilar electroflux refining furnace (ESR), such as mobile mould ESR melting or ESR coating or spray forming technology etc.
The ingot casting that uses the solidification rate described in the above-mentioned arbitrary embodiment of the present invention and chemical composition to make has following characteristic:
-very thin dendrite macrostructure
-uniform chemical property
-there is no dark vein (veining) and a macrosegregation in the middle layer
-there is no a less important segregation
In addition, the ingot casting that uses technique of the present invention to make has the following advantages to rolled products:
-eliminated " orange peel " effect (it is made of the outward appearance of the dendrite pattern that the wearing and tearing difference in zone, interdendritic forms)
-there is no a pin hole problem
-very bright surface smoothness (finish)
The homogeneity of-the surface tissue that obtains by surface working
-there be not a vestige relevant with tissue odds one
In one embodiment of the invention, electroflux refining furnace (ESR) is for the manufacture of ingot casting 34 of the present invention, and schematic diagram is asked for an interview Fig. 4.
Electroflux refining furnace (ESR) can carry out melting with about 300～1100kg/h, and comprises electrode holder 36, thrusts section 38, electrode 40, cooling jacket outlet 42, obtains the cooling jacket entrance 50 of water coolant.In ESR, ingot casting forms by smelting electrode 40, therefore forms different layers in ingot casting material 48, for example is positioned at electrode neighbouring molten slag bath 44 and pool of molten metal 46.
ESR also comprises the start-up plate 52 that is subjected to water-cooled 54, sees Fig. 4.The initial ingot casting (electrode 40) that the ESR technology may need remelting to obtain by conventional melting technology is to form ingot casting 48 of the present invention.Carefully control the remelting of using ESR to carry out, to obtain the average solidification rate according to the embodiment of the present invention, for example during ingot casting forms in working lining and core higher than the average solidification rate of 15 ℃/min.
Therefore, electrode 40 by for example high current heating of an electric current, with the steel of resmelting electrode, thereby forms ingot casting of the present invention in ESR technique.The high current of careful control electrode 40, to control remelt speed, this also affects speed of cooling, thereby affects solidification rate.Solidification rate depends on the ampere electric current that is supplied to electrode according to predefined function (function).Basically, ampere electric current is higher, supplies with the power of resmelting electrode 40 with regard to higher (seeing Ohm's law).The power of supplying with is higher, and the slag temperature is higher, and solidification rate is lower.
By keeping correct remelting speed and slag temperature, can obtain directional freeze with solidification rate of the present invention in working lining and core, simultaneously cooling ingot casting in certain interval.For example, in one embodiment, in the working lining of ingot casting and core solidification rate on average all higher than 15 ℃/min, cooling ingot casting in the freezing range of 1400 ℃～1200 ℃ simultaneously.
According to the present invention, as the technique of the innovation concept and the result of composition of steel combination, the eutectic carbides content in ingot casting is retained as lower than 5% volume percent.This makes the gained roller obtain good grindability index.The grindability index of roller is important, because between the usage period of final roller, grinding is that acquisition is for the important step of the abundant roughness of the roller of cold-rolling process.The concentration that is known that eutectic carbides can give this roller not satisfied grindability index higher than 5%.
In addition, another effect of low eutectic carbides content is that to form the operating period of roller in milling train (mill) trend of dust low.Under contrast, may form dust in the high roller of carbide concentration, this is disadvantageous to the Working environment in rolled products and milling train.
When making ingot casting from the composition that comprises high-caliber Cr (for example 7～13%), control solidification rate and be even more important.Solidification rate is crossed the high segregation that obtains when slow makes high chromium ingot casting produce defective.
When making ingot casting in the freezing range solidification rate higher than 15 ℃/min hang down the segregation rate, thereby obtain the eutectic carbides content lower than 5% volume percent.
By being more readily understood the present invention with reference to following example.Yet these examples are intended to illustrate that ingot casting of the present invention forms the modification of the embodiment of step, and should not be construed as is be used to limiting the scope of the invention.
Comparative example
The impact of example 1 explanation method of the present invention on the microstructure of roller 1 of the present invention.Example 2 is comparative examples.These examples are carried out during producing full scale roller sample (prototype).Experiment shows the distribution of the eutectic carbides in ingot casting after casting and network shape according to the solidification rate generation significant variations of using, and sees the example 1,2 and table 2 of below.Being distributed according to being kept in the final roller after forging of the present invention and tempering of the network shape of seeing in ingot casting and eutectic carbides.
Example 1
This example show form ingot casting 34 of the present invention during when using solidification rate higher than 15 ℃/min on the impact of the microstructure of roller of the present invention.
Fig. 5 A～5B shows and uses average solidification rate when being cooled to 1200 ℃ from 1400 ℃ is the example of the microstructure of the ingot casting of the present invention 1 made of the technique of 50 ℃/min (in the 90mm depths of ingot casting).Eutectic cell in example ingot casting 1 of the present invention little (940,942), Fig. 5 B shows the fragment network with open eutectic net.For the different freezing ranges of solidificating period in the ingot casting different piece, referring to Fig. 8, show the temperature speed on core 82, middle radius 84,90mm place 86,50mm place 88,30mm place 90 and surface 92.Fig. 5 B is the enlarged view of Fig. 5 A.Separately see Table 2.
Fig. 6 A～6B shows and uses average solidification rate when being cooled to 1200 ℃ from 1400 ℃ is the example of the microstructure of the ingot casting of the present invention 2 made of the technique of 18 ℃/min (in the 90mm depths of ingot casting).Fig. 6 A and 6B show the eutectic cell in example ingot casting 2 of the present invention, and they are little, see for example cross-sectional distance 1024.For the different freezing ranges 80 of solidificating period in the ingot casting different piece, referring to Fig. 9, show the temperature speed on core 100, middle radius 102,90mm place 104,50mm place 106,30mm place 108 and surface 110.Fig. 6 B is the enlarged view of Fig. 6 A.Separately see Table 2.
Conclusion
Method of the present invention is guaranteed not have segregation at the middle radius of ingot casting.Do not exist segregation to guarantee the integrity of roller during hardening process at middle radius (or the inboard part of the diameter of cylindrical roller 5/6).Therefore, the solidification rate higher than 15 ℃/min in working lining generates thinner microstructure, and it is as above illustrated, and is better with regard to grinding and dust pollution, sees Fig. 5 A～5B and Fig. 6 A～6B.
Example 2
This example shows the effect of using lower than the solidification rate of 15 ℃/min during test 1 ingot casting forms.
Fig. 7 A～7C shows the example in the microstructure of test 1 ingot casting of making lower than the technique of 15 (in fact even lower than 10) ℃/min with solidification rate in the cooling ingot casting in the freezing range of 1400 ℃ to 1200 ℃.Colony 700 sizes that are used for test 1 ingot casting relatively shown in Fig. 7 A～7C are larger, see for example cross section 708, and it has the cross-sectional length 708 greater than the maximum cross-section of the ingot casting 1 in example 1 of the present invention for example.Test 1 ingot casting and also present shrinkage porosite 704.Also can see thick polymerization eutectic net 702 in Fig. 7 A～7C.Separately see Table 2.Fig. 7 B～7C is the enlarged view of Fig. 7 A.
Conclusion:
Solidification rate lower than 15 ℃/min in the freezing range causes middle radius place's carbide of test 1 ingot structure and high segregation and the shrinkage porosite 704 of thick carbide network 702, sees Fig. 7 A～7C.The high segregation of thick carbide network and carbide becomes fragile openpore roller (white blank roll) or the final roller made according to the ingot casting of test 1, therefore is easy to blast during induction hardening (openpore roller) or cold rolling processing (final roller).
Thick when example 2 also shows solidification rate lower than 15 ℃/min and also makes the size of eutectic cell structure make ingot casting than by the solidification rate higher than 15 ℃/min according to the present invention.
When making ingot casting in the freezing range solidification rate higher than 15 ℃/min hang down the segregation rate, thereby obtain the eutectic carbides content lower than 5% volume percent.
Table 2
Table 2 shows at ingot casting 90mm depths from 1400 ℃ to 1200 ℃ in cooling ingot casting with the experimental data of the average solidification rate of difference (*) test ingot casting.
Comparative example
Thereby the chemical composition that example 3 is used for illustrative examples such as method of the present invention and ingot casting is on the impact on roller of the present invention of the microstructure of ingot casting.Example 4 is comparative examples.Example 3 and 4 shows the microstructure of testing the ingot casting of generation in the laboratory with controlled freezing device and controlled speed of cooling.
The impact of the chemical composition that in ingot casting, the shape of eutectic carbides net is used separately sees Table 3.
Example 3
This example show the method according to this invention in the laboratory to test the microstructure of the ingot casting 1 that is generated in controlled freezing device and freezing range higher than the controlled speed of cooling of 15 ℃/min.When used according to the invention when comprising the chemical composition of 1.4%Mo, obtain open eutectic carbides system 750 in ingot structure, see Figure 10 A～10B.Separately see Table 3.This opening eutectic carbides system 750 that observes in roller 1 according to the present invention is characterized by the dendrite pattern, and Microstructures of Eutectic Carbides 752 does not form the eutectic carbides net (such as such in comparative example 4, test 2) of sealing, but form dendritic arm in network, see Figure 10 A～10B, it shows the microstructure picture of the ingot casting that contains 1.4%Mo that generates according to technique of the present invention.This opening eutectic carbides of the present invention system makes roller easily grind than the roller that the Mo that uses content higher than 1.6% makes.
Example 4
Test 2 ingot castings and use technique of the present invention to make, in its composition, main ingredient corresponding to above-described embodiment, is being different from the present invention but difference is chemical composition aspect the content of Mo.These test 2 ingot castings be the method according to this invention in the laboratory with in controlled freezing device and freezing range higher than the controlled speed of cooling of 15 ℃/min test generated.In test 2, the content of Mo is 2.77%, separately sees Table 3.Using the chemical composition comprise 2.77% Mo to generate ingot casting in technique of the present invention makes the eutectic carbides system of ingot casting be configured as sealing eutectic carbides colony, see Figure 11 A～11B, and eutectic carbides 852 forms the parts 850 of basic isolation, as isolated in Figure 11 A～11B of the microstructure that test 2 is shown or separate colony structure.White area in Figure 11 A～B represents matrix, is mainly iron, and the black area is time level carbide.
The excessive interpolation of testing 2 interalloy elements causes forming thick carbide network, is linked to the segregation of carbide.Separately see Table 3.
Table 3
Table 3 shows from 1400 ℃ of experimental datas with the average solidification rate of difference (*) test ingot casting to 1200 ℃ of cooling ingot castings the time.Component except Mo is in above-mentioned interval.
Step 18: described ingot casting 34 is forged into roller 1
In typically used of the present invention, then the ingot casting 34 that previous step according to the present invention is made is forged.In one embodiment of the invention, ingot casting 34 is carried out forge hot press, method is the known technique of use itself, makes them by between forging hammer and hammer anvil, reduces simultaneously section area and changes shape, ingot casting is formed roller 1 of the present invention.Heat ingot casting in special furnace, see that Figure 12 is to watch the schematic diagram that forges step.
Forging step 18 according to the present invention comprises the following steps, and sees Figure 12:
After the preheating (step 56) of ingot casting 1, the forging ratio of use 1.35～2.0 is forged (step 60).Repeat to forge step 60 and pre-heating step 56, this forging cycle is commonly referred to as a heat (heat) 58.Press desired times and repeat heat 58, to form roller of the present invention, see Figure 12.
In one embodiment, use 3～6 heats 58, ingot casting is forged into roller stock, and forges roller 1 of the present invention.Roller stock is a kind of like this roller, and it has the shape of roller but roll body also lacks final processing to become the roller that can use in milling train.
In another embodiment, ingot casting 34 is forged some heats 58, sees that Figure 13 is to watch the schematic diagram of forged roll:
A) at first, regulate the section area of ingot casting 34 in several or 1～2 heat 58,
B) make a neck of roller in a heat,
C) forge another neck of roller in next heat.
Forge that composition of steel of the present invention is more difficult to carry out, because compared with the Standard Steel trade mark that forges example, alloy content of the present invention is high.
During forging, ingot casting 34 diameter 32 when being forged into roller 1 of the present invention reduces 30～50%.For example, the diameter 2 of roller 1 of the present invention is preferably 250～800mm, see Fig. 1, and the diameter 32 of ingot casting of the present invention 34 is preferably 400～1000mm or 450～1100mm.
Importantly the expectation eutectic carbides microstructure of ingot casting 34 is forming in the manufacturing processed of ingot casting 34 during coagulation step 80.Show be can with forge hot pressure technology forge have eutectic carbides microstructure of the present invention, eutectic carbides content is lower than the ingot casting 34 of 5% volume percent.Use for example can make these big rollers set off an explosion during induction hardening or in milling train with the ingot casting that the solidification rate lower than 15 ℃/min forms with other technique.
Step 20: described roller 1 is carried out preliminary thermal treatment
In manufacturing process of the present invention, with preliminary heat treatment step treatment tube.In one embodiment of the invention, roller is heated to 700 ℃～1100 ℃ in a stove during preliminary thermal treatment 20 of the present invention, then remains on this temperature and reaches certain hour, until gratifying hydrogen diffusion has occured.Carrying out preliminary thermal treatment (normalizing and Spheroidizing Annealing) is in order to improve the workability of roller.
Step 22: described roller is carried out roughing 22
In manufacturing process of the present invention, by roughing step 22 treatment tube.Roller formed according to the present invention 1 is carried out the skin that roughing 22 refers to remove forged roll.In one embodiment of the invention, skin is removed during roughing.Roller is known as black base (black blank) before roughing is processed.By removing zone of oxidation on the roller surface, so black base roller is transformed into openpore.
Step 24: described roller 1 is carried out induction hardening
In manufacturing process of the present invention, come treatment tube by induction hardening.During the induction hardening of roller, form the hard surface of roller.See that Figure 14 is to watch the schematic diagram of induction hardening step.
In one embodiment of the invention, during the induction hardening step, downward slowly mobile roller in the electric voltage frequency that applies 50～1000Hz by inductor assembly 70 or electric current.After heating steps, use water-cooled 72 cooling rollers 1, see Figure 14.Formed hard surface also referred to as the working lining 4 of roller, is approximately 1/6 (the seeing Fig. 1, label 6) of the whole diameter 2 of roller 1.The roller face when a series of inductor block that comprises the wire loop in guiding the chilling case into is passed in decline by rapid heating.The Rapid Thermal infiltration of induction heating forms at roll surface with the chilling that and then makes water has the predetermined layer of uniform rigidity.The neck of roller and core remain on low temperature in whole process.During induction hardening, the frequency that applies to the surface of roller 1 is generally 50～1000Hz, and gives the darker working lining of roller 14 from the frequency than selecting lower part in this interval.The other factors that affects the degree of depth of formed working lining has the gap of (if having used a plurality of inductor blocks) between inductor block 70.In addition, the gap between inductor block 70 and roller 1 or spacing also affect the degree of depth of formed working lining 4.Induction hardening step 24 of the present invention can for once, twice or more times.
Roller of the present invention is blasted when using conventional hardening technique, and induction heating is the proper technology be used to the roller of the present invention that hardens.During induction hardening 24, pair roller 1 cooling is that cold water by large flow carries out.
In one embodiment of the invention, induction hardening 34 is completed by twice induction hardening, and the rear pair roller 1 of induction hardening 24 cooling is to be that 40 ℃ and feed flow are about 300m by temperature
3The large flow water of/h is completed, and roller is that speed with 0.3～1mm/s moves down.
In one embodiment, induction hardening step 24 0.5～2h consuming time.
Step 26: described roller is carried out tempering
In manufacturing process of the present invention, pair roller 1 carries out tempering.The purpose of tempering step is the fragility that reduces roller, and regulates the firmness level.Tempering step 26 is the committed steps during roller forms, because it reduces internal stress.During tempering step, roller obtains the secondary precipitation of final microtexture and carbide by diffusion.Apply air cooling between the tempering heating steps.Preferably carry out 3 tempering at 450～530 ℃ of pair rollers.Tempering step obtains higher than 780HV roller or is the required firmness level of 780～840HV.Accurate control to temperature and time during tempering process is very crucial, such as very balanced microstructures such as tempered martensites, the roller that makes technique according to the present invention make comprises that after tempering the residual ratio of austenite is lower than the tempered martensite of 5% volume percent with acquisition.
Step 28: described roller is processed
In manufacturing process of the present invention, preferably process by procedure of processing 28 pair rollers before being used for milling train.For example, at milling train, wait process of surface treatment to come pair roller to use specific surface treatment by grinding, with roughness and the relevant friction that obtains expectation on the surface of roller.The surface-treated example of pair roller for example has: laser beam surface working (LBT), electron beam surface working (EBT) or electric discharge surface processing (EDT).
In one embodiment, come treatment tube by grinding and electric discharge surface processing (EDT) surface treatment.Figure 15 A～15B shows the surface microhardness of roller after electric discharge surface processing that comprises low chromium component.Figure 15 C～15D shows the surface microhardness of roller of the present invention after electric discharge surface processing.Below white layer 300 in Figure 15 D, there be again layer and the thinner softening zone of austenitizing, because this trade mark has high tempering temperature.Also be pointed out that, in the white layer of Figure 15 D, eutectic carbides 302 is not subjected to the impact of arc energy.Be used for relatively, the carbide of these classifications does not exist in the roller shown in Figure 15 A～B.Roller of the present invention (sees that Figure 15 A～15B) has better character and performance, because have the hard eutectic carbides in white layer than standard brand roller.
Figure 18 shows the more schematically figure of Figure 15 D, shows the microstructure of roll surface of the present invention, wherein at the eutectic carbides 302 of white layer 304 interior existence because of the new formation of remelting.In addition, also show the eutectic carbides 300 of previous formation in Figure 18.How roll surface in Figure 18 shows the surface of carrying out according to the present invention after electric discharge surface is processed seems.Graduated scale 306 represents 5 μ m.
The roller 1 of making by above-mentioned technique of the present invention
The diameter of typical roller of the present invention is 215～800mm or 250～700mm, comprises the whole length of neck up to 6 meters, and its middle cylinder body length is 1～3 meter.The typical weight of roller is 400～10000kg.The microstructure of the roller of one embodiment of the invention is characterised in that and comprises the residual ratio of austenite lower than the tempered martensite of 5% volume percent, and its central roll comprises the open eutectic carbides net less than 5% volume percent eutectic carbides; And roller 1 presents the hardness of 780～840HV; With-300 to-500MPa internal compression stresses.These character of roller be due to roller production technique of the present invention and according to the present invention the chemical composition of the roller of chemical composition.
Roller of the present invention is intended to can bear for demand the cold-strip mill of the roller of high pressure.Roller intention of the present invention is used as working roll in cold-strip mill, and be applicable to any frame (stand) in rolling technology, and be applicable to 2Hi～6Hi milling train, and can have from the teeth outwards the roughness of 0.3～0.5 μ m of demand in finishing stand, to the roughness of 1.5～2.5 μ m of demand in pony roughing mill.
By being more readily understood the present invention with reference to following example.Yet these examples are intended to illustrate the character of roller of the present invention, are be used to limiting the scope of the invention and should not be construed as.
In table 4, differential roller and roller of the present invention are compared.All rollers all comprise the Mn that content is 0.2～0.5% (weight).
Two examples of the present invention
Roller of the present invention 1 in table 4 uses technique of the present invention to make, the solidification rate of use in the freezing range in working lining higher than 15 ℃/min, and the induction heating frequency of using is 50～250HZ, and carries out 3 tempering at 450～530 ℃.
Roller of the present invention 2 in table 4 uses technique of the present invention to make, the solidification rate that uses is 18 ℃/min in working lining in the freezing range, and the induction heating frequency of using is 50～250HZ, and carry out 3 tempering, carry out at 490 ℃ for the first time, then carry out at 490 ℃, last tempering carries out at 480 ℃.Figure 19 A and 19B show the microstructure of roller after tempering and induction hardening, and sample is taken at the surperficial 4mm depths apart from roller 2.Also show the eutectic carbides 1032 of roller in Figure 19 A～19B and have the microstructure 1034 of open eutectic net.
Table 4
The Mn content of table 4 central roll is all in 0.4～0.5 scope, and the Si content of table 4 central roll is all in 0.2～2.0 scope, and Ni is always lower than 1%.
The application of roller
The applicable application of roller has:
Aluminium industry:
The irreversible milling train of-single chassis 4Hi
Steel industry:
-4Hi single chassis is reversible
-4Hi tandem 4 and 5 frames are for the sheet material of continuous and discontinuous technique
-4Hi tandem 4 and 5 frames are used for tin plate
-6Hi tandem mill is used for sheet material
The roller purposes
Forged roll of the present invention is suitable for use as working roll in cold-rolling mill for example or intermediate roll or for example:
-be used for the cold rolling attenuate milling train of reversible and irreversible frame, roughing and the finishing stand of tin plate, sheet material, silicon steel, aluminium or copper.
-cold rolling tempering and/or skin-pass milling train;
-be configured to have and processed or the undressed milling train of two rollers (High), four rollers and six roller frames on surface excessively.
-AHSS (Advanced High Strength Steel, AHSS) grade of steel cold rolling.
Roll surface
Surface tissue
A problem of existing roller is that surface tissue wore and tore between the usage period of roller.Surface tissue is important, because it guarantees frictional coefficient, to avoid skidding and/or derailing of band.In addition, it determines the surface tissue of band, and it gives the deep-drawing of rolled strip and the vital surface properties of japanning.Roller of the present invention presents the ability of their surface tissue of maintenance of increase because of the white layer of roller, wherein white layer comprises as M
7C
3The hard eutectic carbides.In working lining, the microstructure of roller of the present invention after final thermal treatment by the residual ratio of austenite lower than the tempered martensite of 5% volume percent and slightly and in being evenly distributed in matrix as MC and M
2The carbide of C (M=metal, C=carbon) consists of.This microstructure has shown the surface tissue that keeps roller very important.
Roughness shifts
The roughness of roll surface shifts (roughness transfer) and changes between the usage period of roller.The roughness that keeps during rolling that roller of the present invention presents increase shifts constant ability, and the life-span of this pair roller is very important.This is due to the composition of special requirement and the production method used when making roller.
In milling train, free program is rolling
A problem during the use roller is that the dirt that accumulates on roll surface stays trajectory on band.In working lining, roller of the present invention has strong surface because the microstructure of roller of the present invention comprise the residual ratio of austenite lower than the tempered martensite of 5% volume percent and slightly and be evenly distributed in matrix as MC and M
2The carbide of C, wherein M represents metal and C represents carbon.This special microstructure increases the rolling possibility of free program.
Scaling
Another problem of existing roller is that the propagation of crackle in roller is by the zone of the residualinternal stress of roller and the caused cumulative stress domination of rolling operation.Roller in use is subject to a complex set of stress.Roller of the present invention demonstrates low-level residualinternal stress, therefore resists better scaling (spalling), and this makes milling train casualty ratio of accidents step-down.
The physical strength of roller of the present invention is more identical from roller of the present invention than alloying constituent but roller that production method is different good.The physical strength of roller of the present invention is due to the open eutectic net that forms in the working lining of roller.This opening eutectic net is to form in cooling step in the roller manufacturing process.The solidification rate higher than 15 ℃/min when making ingot casting in cooling step is most important to the formation that is present in the open network in roller of the present invention.
The accumulation of each temper of carrying out at the production period of the roller high temperature after the sclerosis of 450～530 ℃ for example in addition, causes internal stress important lax of roller.Internal stress is by being minimized outer field differential heating.The penetration of hardness of roller of the present invention can be controlled in from roll surface and inwardly measure between 20～120mm on diameter.The internal compression stresses of roller of the present invention is being preferably between-300 to-500MPa or for example lower than-400MPa on absolute value.
The microstructure of roller
Figure 17 A shows the schematic diagram of the present invention's one example roller microstructure.Can see dendritic arm 210 in Figure 17 A, be consisted of by eutectic carbides, form eutectic cell structure 204 by forming open carbide network.The open eutectic net that is made of dendritic arm 210 of appreciable formation eutectic cell 204 forms in technique because of peculiar chemical composition of the present invention in Figure 17 A.Graduated scale 208 represents 100 μ m.
In one embodiment of the invention, the microstructure of roller of the present invention comprises a crystal grain only covering colony structure or the open eutectic net of two crystal grain.
By contrast, Figure 17 B shows sealing eutectic net, and wherein eutectic carbides 200 forms the sealing eutectic net that eutectic cell 212 obviously separates.This net is undesired in roller of the present invention, because if roller has comprised this microstructure, can become fragile.Graduated scale 214 represents 100 μ m.
Abovely by the different embodiment in the scope that is in claims, the present invention has been described.
Claims (42)
1. the roller of a forging (1), comprise a kind of composition of steel, and this composition of steel comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
The microstructure of wherein said roller (1) comprising:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% (volume);
And wherein said roller (1) presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
2. roller as described in above-mentioned claim, wherein, described open eutectic carbides net defines the eutectic cell of colony shape apperance.
3. roller as described in any one in above-mentioned claim, wherein, described open eutectic carbides net comprises dendritic arm.
4. roller as described in any one in above-mentioned claim, wherein, described microstructure is present in the working lining of described roller at least.
5. roller as described in any one in above-mentioned claim, its composition of steel is composed as follows with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
Ni less than (＜) 1%
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2
Less than the W of (＜) 2%, and
Less than the Nb of (＜) 1%, and
Less than the Ti of (＜) 1%, and
Less than the Ta of (＜) 0.5%, and
Less than the Zr of (＜) 0.5%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity.
6. roller as described in any one in above-mentioned claim, wherein, the C content in described composition of steel account for regard to weight percent whole roller heavy 0.8～0.99%.
7. roller as described in any one in above-mentioned claim, wherein, the C content in described composition of steel account for regard to weight percent whole roller heavy 0.85～0.9%.
8. roller as described in any one in above-mentioned claim, wherein, the Mn content in described composition of steel account for regard to weight percent whole roller heavy 0.4～0.5%.
9. roller as described in any one in above-mentioned claim, wherein, the Si content in described composition of steel account for regard to weight percent whole roller heavy 0.2～1.5%.
10. roller as described in any one in above-mentioned claim, wherein, the Si content in described composition of steel account for regard to weight percent whole roller heavy 0.85～1.15%.
11. roller as described in any one in above-mentioned claim, wherein, the Cr content in described composition of steel account for regard to weight percent whole roller heavy 7.0～11%.
12. roller as described in any one in above-mentioned claim, wherein, the Cr content in described composition of steel account for regard to weight percent whole roller heavy 7.3～less than (＜) 8.0%.
13. roller as described in any one in above-mentioned claim, wherein, the Mo content in described composition of steel account for regard to weight percent whole roller heavy 1.45～1.55%.
14. roller as described in any one in above-mentioned claim, wherein, the Ni content in described composition of steel account for regard to weight percent whole roller heavy less than (＜) 0.3.
15. roller as described in any one in above-mentioned claim, wherein, the V content in described composition of steel account for regard to weight percent whole roller heavy 1.3～2.1%.
16. roller as described in any one in above-mentioned claim, wherein, the V content in described composition of steel account for regard to weight percent whole roller heavy 1.3～1.6%.
17. roller as described in any one in above-mentioned claim, wherein, described composition of steel component with regard to weight percent is as follows:
0.8～0.99% C, and
0.4～0.5% Mn, and
0.2～1.5% Si, and
7.0～11% Cr, and
0.6～1.6% Mo, and
Less than the Ni of (＜) 1.0, and
1.0～2.1% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
18. roller as described in any one in above-mentioned claim, wherein, described composition of steel component with regard to weight percent is as follows:
0.85～0.9% C, and
0.4～0.5% Mn, and
0.85～1.15% Si, and
7.3～less than the Cr of (＜) 8.0%, and
1.45～1.55% Mo, and
Less than the Ni of (＜) 0.3, and
1.3～1.6% V, and
Less than the P of (＜) 0.015%, and
Less than the S of (＜) 0.015%, and
O less than (＜) 30ppm
2, and
N less than (＜) 100ppm
2, and
H less than (＜) 3ppm
2, and
The remainder of roller be mainly Fe and may trace and/or inevitable impurity.
19. roller as described in any one in above-mentioned claim further is structured as the working roll in cold rolling.
20. roller as described in any one in above-mentioned claim further has the weight greater than 400kg.
21. roller as described in any one in above-mentioned claim further has the diameter in 215～800mm scope.
22. the technique for the manufacture of non-forged roll comprises the following steps:
A., a kind of composition of steel is provided, and it comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
B. make ingot casting, keep the solidification rate higher than 15 ℃/min in the freezing range in the working lining of ingot casting;
C. this ingot casting is forged into roller;
D. make the roller sclerosis by induction heating;
E. with the temperature of 450～530 ℃, described roller is carried out tempering to reach the hardness of 780～840HV;
Thereby obtain the microstructure of described roller (1), it comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And wherein said roller (1) presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
23. technique as claimed in claim 22, wherein, the solidification rate of working lining and core is maintained 15 ℃/min～55 ℃/min or 17 ℃/min～50 ℃/min or 35 ℃/min～55 ℃/min or 45 ℃/min～55 ℃/min, make ingot casting.
24. technique as described in any one in claim 22-23 wherein, is kept the solidification rate higher than 35 ℃/min in the working lining of freezing range at ingot casting, make ingot casting.
25. technique as described in any one in claim 22-24, wherein, for described ingot casting, described freezing range is 1400～1200 ℃.
26. technique as described in any one in claim 22-25 wherein, by the predefined function control ampere electric current source according to solidification rate, is kept the solidification rate of selecting in advance, thereby is made ingot casting in the electroflux refining furnace technical matters.
27. technique as described in any one in claim 22-26, wherein, the step that ingot casting is forged into roller comprises the following steps:
A. ingot casting is heated to 800～1200 ℃ or 850～1100 ℃, preferably continues approximately 6 hours;
B. higher than 800 ℃ or forge described ingot casting higher than the temperature of 850 ℃;
C. repeating step a～b is until described ingot casting forms the roller with intended shape and size.
28. technique as described in any one in claim 22-27 also comprises preliminary heat treated step after forging step, the temperature of preferably to 700～1100 ℃ or 800～900 ℃ can comprise the hydrogen DIFFUSION TREATMENT.
29. technique as described in any one in claim 22-29, wherein, the step that pair roller carries out tempering comprises the following steps:
A. heat described roller to approximately 450～530 ℃, preferred 3 times,
B. between each heating steps, described roller is carried out air cooling.
30. technique as described in any one in claim 22-29 also comprises described roller is carried out mechanical workout, comprises the white layer of eutectic carbides with processing.
31. technique as described in any one in claim 30, wherein, the eutectic carbides in described white layer is from M
7C
3In select.
32. technique as described in any one in claim 22-31 also comprises the feature of any one in claim 1-21.
33. the roller of a forging (1) is generated by the technique that comprises the following steps:
A., a kind of composition of steel is provided, and it comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
B. make ingot casting, keep the solidification rate higher than 15 ℃/min in the freezing range in the working lining of ingot casting;
C. this ingot casting is forged into roller;
D. make the roller sclerosis by induction heating;
E. pair roller carries out tempering;
Thereby obtain the microstructure of described roller (1), it comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent;
And wherein said roller (1) presents:
The hardness of-780～840HV; With
--300 to-500MPa internal compression stresses.
34. roller as claimed in claim 33 also comprises the feature of any one in claim 1-32.
35. the intermediates ingot casting in a kind as above-mentioned claim 1-34 in the production process of the described roller of any one comprises a kind of composition of steel, this composition of steel comprises with regard to weight percent:
0.8 to the C less than (＜) 1%,
0.2～0.5% Mn,
0.2～2.0% Si,
7.0～13.0% Cr,
0.6～1.6% Mo,
Greater than the V of (＞) 1.0～3.0%,
The remainder of steel be mainly Fe and may trace and/or inevitable impurity;
And the microstructure of the final roller of wherein making from described ingot casting comprises:
The residual ratio of-austenite is less than the tempered martensite of (＜) 5% volume percent; With
-eutectic carbides is less than the open eutectic carbides net of (＜) 5% volume percent.
36. an as above described intermediates ingot casting of claim also comprises the feature of any one in claim 1-34.
37. as the purposes of the described roller of any one in claim 1-21 or 33-34, be used for material cold rolling of the high rolling load of demand.
38. as the purposes of the described roller of any one in claim 1-21 or 33-34, be used for cold rolling such as high-strength materials such as AHSS grades of steel.
39. the purposes as the described roller of any one in claim 1-21 or 33-34 is used for:
-be used for the cold rolling attenuate milling train of reversible and irreversible frame, roughing and the finishing stand of tin plate, sheet material, silicon steel, stainless steel, aluminium and copper; Or
-cold rolling tempering and/or skin-pass milling train; Or
-be configured to have and processed or the undressed milling train of two rollers, four rollers and six roller frames on surface excessively.
40. as the purposes of the described roller of any one in claim 1-21 or 33-34, as working roll.
41. as described in any one in above-mentioned claim: the purposes of the roller that roller, technique are produced, the production technique of roller and/or roller, wherein said roller is without coating.
42. as described in any one in above-mentioned claim: the purposes of the roller that roller, technique are produced, the production technique of roller and/or roller, wherein said roller coat is covered with optional coating, for example chromiumcoating.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/SE2011/050246 WO2012121630A1 (en) | 2011-03-04 | 2011-03-04 | A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103108975A true CN103108975A (en) | 2013-05-15 |
| CN103108975B CN103108975B (en) | 2015-11-25 |
Family
ID=46798429
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201180000136.7A Active CN103108975B (en) | 2011-03-04 | 2011-03-04 | Meet forged roll and the production method thereof of cold rolling industrial requirement |
Country Status (5)
| Country | Link |
|---|---|
| CN (1) | CN103108975B (en) |
| AU (1) | AU2011361937B2 (en) |
| CA (1) | CA2828894C (en) |
| RU (1) | RU2572269C2 (en) |
| WO (1) | WO2012121630A1 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106191703A (en) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | A kind of high-chromium wear-resistant steel ball and preparation method thereof |
| CN111593259A (en) * | 2020-05-20 | 2020-08-28 | 樟树市兴隆高新材料有限公司 | Valve steel and preparation method thereof |
| CN112238143A (en) * | 2019-07-16 | 2021-01-19 | Posco公司 | Heat pipe roller based on forging roller and manufacturing method thereof |
| CN112410673A (en) * | 2020-11-18 | 2021-02-26 | 宝钢轧辊科技有限责任公司 | High-speed steel roll for rolling ultrahigh-strength steel plate and manufacturing method thereof |
| CN115074625A (en) * | 2022-06-23 | 2022-09-20 | 宝钢轧辊科技有限责任公司 | Intermediate roll of sendzimir mill and its manufacturing method |
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| DE102014217369A1 (en) * | 2014-09-01 | 2016-03-03 | Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. | HIGH STRENGTH, MECHANICAL ENERGY ABSORBING AND CORROSION-RESISTANT FORM BODIES OF IRON ALLOYS AND METHOD FOR THE PRODUCTION THEREOF |
| CN104313477B (en) * | 2014-10-10 | 2017-10-13 | 绵阳西诺特矿用设备制造有限公司 | A kind of high abrasion steel and its application |
| BR102015027438B8 (en) * | 2015-10-29 | 2021-12-21 | Inst De Pesquisas Tecnologicas Do Estado De Sao Paulo S/A | Piston rings in cast tool steels and their manufacturing process |
| CN112792304B (en) * | 2020-12-07 | 2023-05-05 | 邢台德龙机械轧辊有限公司 | Preparation method of large chromium alloy strip steel supporting roller |
| US11566299B2 (en) * | 2021-02-01 | 2023-01-31 | L.E. Jones Company | Martensitic wear resistant alloy strengthened through aluminum nitrides |
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Also Published As
| Publication number | Publication date |
|---|---|
| AU2011361937B2 (en) | 2015-10-01 |
| AU2011361937A1 (en) | 2013-10-03 |
| CA2828894A1 (en) | 2012-09-13 |
| WO2012121630A1 (en) | 2012-09-13 |
| RU2013142706A (en) | 2015-04-10 |
| CA2828894C (en) | 2017-05-09 |
| RU2572269C2 (en) | 2016-01-10 |
| CN103108975B (en) | 2015-11-25 |
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