CN103108975B - Meet forged roll and the production method thereof of cold rolling industrial requirement - Google Patents

Meet forged roll and the production method thereof of cold rolling industrial requirement Download PDF

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Publication number
CN103108975B
CN103108975B CN201180000136.7A CN201180000136A CN103108975B CN 103108975 B CN103108975 B CN 103108975B CN 201180000136 A CN201180000136 A CN 201180000136A CN 103108975 B CN103108975 B CN 103108975B
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roller
less
ingot casting
steel
present
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CN103108975A (en
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克劳德.加斯帕德
凯瑟琳.沃格尼
丹尼尔.巴塔齐
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AAKERS AB
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AAKERS AB
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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
    • 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
    • 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
    • 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
    • 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
    • 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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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates in general to the field of forged roll and the production of forged roll.More specifically, the present invention relates to the forged roll for cold rolling industry.The present invention relates to the forged roll for cold rolling industry and the method for producing this roller.Described forged roll comprises a kind of composition of steel and microstructure, and it comprises: austenite is residual than being less than (<) 5% tempered martensite of volume percent; (<) 5% open eutectic carbides net of volume percent is less than with eutectic carbides; And wherein said roller presents: the hardness of 780 ~ 840HV; With the internal compression stresses that absolute value is-300 to-500MPa.

Description

Meet forged roll and the production method thereof of cold rolling industrial requirement
Technical field
The present invention relates in general to the field of forged roll and the production of forged roll.More specifically, the present invention relates to the demand meeting cold rolling industry and be mainly used in the forged roll of cold rolling industry.
Background technology
General background
The general trend of the cold rolling development of iron and non-ferrous metal industry be rolling sooner, thinner and wider.Current challenge completes above-mentioned trend while realizing the planeness of perfect control with high productivity compatibility, thickness and appearance.Therefore, this trend requires to use the advanced rolling technique controlling crucial rolling parameter.
Such as some key parameters such as roughness confining force and appearance can be guaranteed by chromium plating working roll.This measure is effectively and efficiently, but is just becoming due to environmental restraint and more and more have problem, and can become unacceptable in the near future.
At present, the working roll (2 ~ 6%Cr) of chrome faced forging is generally used for cold-rolling process.Carrying out chromium plating to this roller is to improve wear resistance with regard to surface tissue confining force, itself so that will such as car body to make peace higher gloss after painting be guaranteed.Hard electrolytic deposition technology as chromium plating is developed in order to the application of tempering/skin-pass (skinpass) milling train at first.In such applications, chromium plating working roll presents than the life-span without long 2 ~ 8 times of coating roller, mainly due to better roughness confining force.The enforcement of this technology extends to thinning milling train (reductionmill) gradually.
In addition, also there is the intention be made up of rapid steel (HSS) without the forged roll used under coating state, but need the roller that residualinternal stress is low, and need the industrial technology producing this roller, for milling train while its intention gives at least to be equivalent to have the roughness confining force of coating roller under uncoated state.
Concrete background
Producing the roller that uses in the industry at Cold-roller must management processing conditioned disjunction concrete operations stress during use, is easy to explode not crack or to become.The blast of roller can relate to collateral damage in the safety of operator and milling train.Therefore, the roller needing residualinternal stress low.
Prior art
To disclose towards the development of uncoated high speed steel roller for the example of the prior art of cold rolling object:
C.Gaspard，C.Vergne，D.Batazzi，T.Nylen，P.H.Bolt，S.Mul，K.M.Reuver：″Implementationofin-servicekeyparametersofHSSworkrollgradededicatedtoadvancedcoldrolling″，ISTConferenceMay3-6，2010，Pittsburgh，Pa，USA
C.Gaspard，S.Bataille，D.Batazzi，P.Thonus：″ImprovementForAdvancedColdRollingReductionMillsByUsingSemi-HSSandHSSRolls″，7thInternationalConferenceonSteelRolling(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.vandenElzen，C.Vergne，I.M.Williams：″DamageResistanceandRoughnessRetentionofworkRollsincoldRollingMills″，5thEuropeanRollingConference，23-25June2009，London，UK
Other of prior art exemplify in present following patent publications: JP09003603, JP53077821, JP57047849, JP2002285284, JP2002285285, JP10317102, JP1208437, EP0395477 and JP08158018, which describe the cold rolling working roll for strengthening wearing and tearing and scaling resistance.
But the open realization of these prior aries is also carried out operating necessary parameter and character under making the condition of this high speed steel rider in cold-rolling mill.
Summary of the invention
Object of the present invention
Overall object
Overall object of the present invention be to provide a kind of can preferably with the roller carrying out operating without coating form and production technique thereof under the condition in cold-rolling mill.More specifically object is to provide a kind of roller and production technique thereof, keep the tribological properties such as the such as low-friction coefficient at least having coating roller suitable with prior art, high roughness confining force, iron powder dust pollution simultaneously, and compared with known roller, with regard in operation compared with the rolling mill characteristic presenting improvement with regard to high cracking resistance and higher-security.
Subproblem
The present invention seeks to solve following subproblem further:
-improve roll surface, give the performance that roller is higher
-avoid roller scaling accident
-roller the production technique avoiding not environmentally
-improve roller rolling distance or the life-span, allow the running that each milling train operation is longer.
Summary of the invention
The solution of the problem more than enumerated, 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 milling train accident while keeping compared with high-wearing feature.
The invention provides a kind of forged roll for cold rolling industry and produce the method for this roller.This roller preferably without coating, but also can have 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 being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity;
The microstructure of wherein said roller comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And wherein said roller presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
In other embodiments of the present invention, roller of the present invention comprises the open eutectic carbides net of the eutectic cell defining 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 (dendriticarm).
A kind of roller, the open eutectic carbides net form of wherein said roller becomes multiple eutectic carbides mesh portions of substantial separation.
A kind of roller, the microstructure of wherein said roller is at least present in the working lining of roller.
A kind of roller, has the composition of steel that component with regard to weight percent is following:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the Ni of (<) 1%
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2
Be less than the W of (<) 2%, and
Be less than the Nb of (<) 1%, and
Be less than the Ti of (<) 1%, and
Be less than the Ta of (<) 0.5%, and
Be less than the Zr of (<) 0.5%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity;
According to roller of the present invention, the C content wherein in composition of steel account for regard to weight percent whole roller heavy 0.8 ~ 0.99%.
According to roller of the present invention, the C content wherein in composition of steel account for regard to weight percent whole roller heavy 0.85 ~ 0.9%.
According to roller of the present invention, the Mn content wherein in composition of steel account for regard to weight percent whole roller heavy 0.4 ~ 0.5%.
According to roller of the present invention, the Si content wherein in composition of steel account for regard to weight percent whole roller heavy 0.2 ~ 1.5%.
According to roller of the present invention, the Si content wherein in composition of steel account for regard to weight percent whole roller heavy 0.85 ~ 1.15%.
According to roller of the present invention, the Cr content wherein in composition of steel account for regard to weight percent whole roller heavy 7.0 ~ 11%.
According to roller of the present invention, the Cr content wherein in composition of steel account for regard to weight percent whole roller heavy 7.3 ~ be less than (<) 8.0%.
According to roller of the present invention, the Mo content wherein in composition of steel account for regard to weight percent whole roller heavy 1.45 ~ 1.55%.
According to roller of the present invention, the Ni content wherein in composition of steel account for regard to weight percent whole roller heavy be less than (<) 0.3.
According to roller of the present invention, the V content wherein in composition of steel account for regard to weight percent whole roller heavy 1.3 ~ 2.1%.
According to roller of the present invention, the V content wherein 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:
The C of 0.8 ~ 0.99%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.2 ~ 1.5%, and
The Cr of 7.0 ~ 11%, and
The Mo of 0.6 ~ 1.6%, and
Be less than the Ni of (<) 1.0, and
The V of 1.0 ~ 2.1%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
The remainder of roller mainly Fe and may trace and/or may inevitable impurity.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
The C of 0.85 ~ 0.9%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.85 ~ 1.15%, and
7.3 ~ be less than the Cr of (<) 8.0%, and
The Mo of 1.45 ~ 1.55%, and
Be less than the Ni of (<) 0.3, and
The V of 1.3 ~ 1.6%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
The remainder of roller mainly Fe and may trace and/or may inevitable impurity.
Roller of the present invention be structured as further cold rolling in working roll.
Roller of the present invention has the weight being greater than 400kg further.
Roller of the present invention has the diameter of 215 ~ 800mm scope further.
Another aspect of the present invention provides the forged roll by the Process Production comprised the following steps:
A. provide a kind of composition of steel, it comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity; In further embodiments, composition of the present invention as mentioned component or composition combination any one as described in;
B. manufacture ingot casting, in freezing range, in the upper layer (being equivalent to the upper layer of roller) of ingot casting, maintain the solidification rate higher than 15 DEG C/min;
C. this ingot casting is forged into roller;
D. by induction heating, roller is hardened;
E. pair roller carries out tempering;
Thus obtain the microstructure of described roller, it comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And wherein said roller (1) presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
Other modification of roller comprises any one in the chemical composition of above-mentioned roller or the following optional, independent or capable of being combined of 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 roller of the present invention, and this technique comprises the following steps:
A. provide a kind of composition of steel, it comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity; In further embodiments, as described in any one that composition of the present invention combines as mentioned component;
B. manufacture ingot casting, in freezing range, in the working lining (being equivalent to the working lining of roller) of ingot casting, maintain the solidification rate higher than 15 DEG C/min;
C. this ingot casting is forged into roller;
D. by induction heating, roller is hardened;
E. with the temperature of 450 ~ 530 DEG C, tempering is carried out to reach the hardness of 780 ~ 840HV to described roller;
Thus obtain the microstructure of described roller (1), it comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And wherein said roller (1) presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
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 DEG C/min ~ 55 DEG C/min or 17 DEG C/min ~ 50 DEG C/min or 35 DEG C/min ~ 55 DEG C/min or 45 DEG C/min ~ 55 DEG C/min, manufacture ingot casting.
According to technique of the present invention, wherein, in the working lining or surface of ingot casting, maintain the solidification rate higher than 35 DEG C/min in freezing range, manufacture ingot casting.
According to technique of the present invention, wherein, for described ingot casting, described freezing range is 1400 ~ 1200 DEG C.
According to technique of the present invention, wherein, predefined function (function) according to solidification rate controls ampere electric current source (amperecurrentsupply), thus in electroflux refining furnace technical matters, maintain the solidification rate selected in advance, manufactures ingot casting.
A kind of technique, the step wherein ingot casting being forged into roller comprises the following steps:
A. ingot casting is heated to about 850 ~ 1100 DEG C or 800 ~ 1000 DEG C, preferably continues about 6 hours;
B. higher than about 800 DEG C or forge described ingot casting higher than the temperature of 850 DEG C;
C. repeating step a ~ b, until described ingot casting is formed as the roller with intended shape and size.
Technique also comprises the preliminary heat treated step applied roller stock after forging step, preferably to the temperature of about 700 ~ 1100 DEG C or 800 ~ 900 DEG C, can comprise hydrogen trap process.
A kind of technique also comprises carries out case-hardened step by progressive induction heating, preferably the temperature of about 900 ~ 1150 DEG C.
A kind of technique, the step that wherein pair roller carries out tempering comprises the following steps:
D. described roller is heated to about 450 ~ 530 DEG C or 450 ~ 520 DEG C, preferably 3 times,
E. between each heating steps, air cooling is carried out to described roller.
A kind of technique, also comprises and carries out mechanical workout to described roller, to process the white that (texturing) comprises eutectic carbides.
Other modification of technique of the present invention comprises any one in the chemical composition of above-mentioned roller or the following optional, independent or capable of being combined of 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 ingot casting of the intermediates 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 being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity;
And the microstructure of the final roller wherein made from described ingot casting comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<).
Other modification of middle ingot casting of the present invention comprise about above-mentioned ingot casting chemical composition following optional, independent or capable of being combined in any one, and comprise 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, for the material of cold rolling demand height rolling loads.
Other embodiments of the present invention provide a kind of purposes of forged roll, cold rolling for high-strength materials such as such as AHSS grades of steel.
According to the purposes of forged roll of the present invention, for following option:
-for the rolled thickness reduction milling train of the reversible and irreversible frame of tin plate, sheet material, silicon steel, stainless steel, aluminium and copper, roughing and finishing stand; Or
-cold rolling tempering and/or skin-pass milling train; Or
-be configured to have the milling train of two rollers on processed or untreated surface, four rollers and six roller frames.
According to forged roll of the present invention be used as working roll.
Roller of the present invention is suitable to be used as in numerous applications without coating roller.But in other and in embodiment, roller also can be provided with coating of the present invention, select for current or specifically apply arbitrarily.Coating can be such as chromiumcoating.Roller also can be used for warm-rolling application.
Accompanying drawing explanation
The present invention will be further described below by illustrating some embodiments, 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 the roller trade mark using production technique of the present invention to make.This roller trade mark is with shown in the sectional view of its working lining.
Fig. 6 A ~ 6B shows the cast microstructure of the roller trade mark using production technique of the present invention to make.This roller trade mark is with shown in the sectional view of its working lining.
But Fig. 7 A ~ 7C shows the cast microstructure that use production technique difference of the present invention is the roller trade mark using too low solidification rate to make.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 made in laboratory conditions when using production technique of the present invention.
Figure 11 A ~ 11B show use production technique of the present invention but the Mo too high levels used time the cast microstructure of ingot casting made in laboratory conditions.
Figure 12 carries out according to the present invention the schematic diagram that forges.
Figure 13 A ~ 13C is the schematic diagram of the step by forging, ingot casting being formed as roller of the present invention.
Figure 14 is the schematic diagram with different frequency, roller of the present invention being carried out to progressive induction hardening.
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 generated when manufacturing 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 closed eutectic net, and wherein eutectic carbides 200 forms the closed eutectic net that eutectic cell 212 is obviously separated.
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 the roller microstructure of the dark place of 4mm on roll surface after the tempering and induction hardening of roller.
Embodiment
Introduce
The present invention relates in general to the forged roll 1 that weight is preferably greater than 400kg or weight is greater than 1000kg as in the embodiment for common application.Roller of the present invention be according to general step itself be known but according to the innovation concept specifically adapt to into can produce roller of the present invention forged roll production method generate.
The present invention relates generally to the roller that weight is 400kg ~ 10000kg.The diameter 2 of roller of the present invention is generally greater than 200mm, such as, be 215 ~ 800mm, and the length of its cylindrical shell 8 is generally 1 ~ 3 meter, and the maximum length comprising neck 10 is generally about 6 meters.Roller 1 has working lining 4, and it corresponds 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, 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, 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.
Special problem and challenge is there is, because the internal stress related to when forming these large roller when manufacturing large forged roll.The roller that diameter is less does not need identical process, because internal stress is now lower, and these rollers are such as not easy to explode between hardening period.
Roller production technique 12 of the present invention is most important to the roller 1 manufacturing size of the present invention.The mechanical property that the such as low residualinternal stress of roller of the present invention etc. improves is obtained by roller production technique 12.In order to the level of the residualinternal stress making gained roller is low, the internal stress that thermal gradient and polymorphic transformation must 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 because of chemical composition of the present invention and roller production technique and comprise austenite and remain than the tempered martensite lower than 5% volume percent.
Roller production technique of the present invention comprises the selected works (selection) of the following basic step schematically shown in the flowchart of fig. 2:
14. provide a kind of composition of steel
16. manufacture ingot casting 34
Described ingot casting 34 is forged into roller 1 by 18.
20. pairs of described rollers 1 carry out preliminary thermal treatment
Roller 1 described in 22. roughing
Roller 1 described in 24. induction hardenings
26. pairs of described rollers 1 carry out tempering heat treatment
The described roller 1 of 28. processing
Intermediates are obtained after each step.Select the chemical composition of concrete controling parameters and roller to produce roller of the present invention.
Roller production technique
The present invention relates to the forged roll 1 of the Process Production by comprising the following steps:
A. provide a kind of composition of steel, it comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity;
B. manufacture ingot casting, in freezing range (interval) working lining at ingot casting, maintain the solidification rate higher than 15 DEG C/min;
C. this ingot casting is forged into roller;
D. by induction heating, roller is hardened;
E. pair roller carries out tempering;
Thus obtain the microstructure of roller 1, it comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And its central roll 1 presents:
-be greater than the hardness of 780HV; With
-absolute value is less than the internal compression stresses of-500MPa.
Wherein the provided chemical composition of the present invention used with combination of process steps of the present invention gives roller of the present invention with the performance expected 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 formed as enumerated in table 1.The effect of the roller of the present invention in table 1, describe the impact of component, being obtained by the component selected and specifically interval.
Table 1
And also comprise content alternatively separately lower than the H of 0.4% (weight) 2, N 2, O 2, Al, Cu; And wherein composition of steel remainder eliminating minute element and inevitably may be mainly Fe outside impurity.
In an embodiment of the present invention, composition of steel comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
Wherein steel remainder eliminating minute element and inevitably may be mainly Fe outside impurity.
In different embodiments of the invention and modified example, composition comprises or construct is combination or the selected works of component (% by weight) according to following example.In some cases, previous embodiment and following group component modified example combine, are replaced by following group component modified example or narrow.
A kind of roller, has the composition of steel that component with regard to weight percent is following:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than the V of (>) 1.0 ~ 3.0%,
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the Ni of (<) 1%
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H2 of (<) 3ppm
Be less than the W of (<) 2%, and
Be less than the Nb of (<) 1%, and
Be less than the Ti of (<) 1%, and
Be less than the Ta of (<) 0.5%, and
Be less than the Zr of (<) 0.5%,
The remainder of steel mainly Fe and may trace and/or may inevitable impurity.
According to roller of the present invention, the C content wherein in composition of steel account for regard to weight percent whole roller heavy 0.8 ~ 0.99%.
According to roller of the present invention, the C content wherein in composition of steel account for regard to weight percent whole roller heavy 0.85 ~ 0.9%.
According to roller of the present invention, the Mn content wherein in composition of steel account for regard to weight percent whole roller heavy 0.4 ~ 0.5%.
According to roller of the present invention, the Si content wherein in composition of steel account for regard to weight percent whole roller heavy 0.2 ~ 1.5%.
According to roller of the present invention, the Si content wherein in composition of steel account for regard to weight percent whole roller heavy 0.85 ~ 1.15%.
According to roller of the present invention, the Cr content wherein in composition of steel account for regard to weight percent whole roller heavy 7.0 ~ 11%.
According to roller of the present invention, the Cr content wherein in composition of steel account for regard to weight percent whole roller heavy 7.3 ~ be less than (<) 8.0%.
According to roller of the present invention, the Mo content wherein in composition of steel account for regard to weight percent whole roller heavy 1.45 ~ 1.55%.
According to roller of the present invention, the Ni content wherein in composition of steel account for regard to weight percent whole roller heavy be less than (<) 0.3.
According to roller of the present invention, the V content wherein in composition of steel account for regard to weight percent whole roller heavy 1.3 ~ 2.1%.
According to roller of the present invention, the V content wherein 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:
The C of 0.8 ~ 0.99%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.2 ~ 1.5%, and
The Cr of 7.0 ~ 11%, and
The Mo of 0.6 ~ 1.6%, and
Be less than the Ni of (<) 1.0, and
The V of 1.0 ~ 2.1%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
The remainder of roller mainly Fe and may trace and/or may inevitable impurity.
According to roller of the present invention, wherein composition of steel component with regard to weight percent is as follows:
The C of 0.85 ~ 0.9%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.85 ~ 1.15%, and
7.3 ~ be less than the Cr of (<) 8.0%, and
The Mo of 1.45 ~ 1.55%, and
Be less than the Ni of (<) 0.3, and
The V of 1.3 ~ 1.6%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
The remainder of roller mainly Fe and may trace and/or may inevitable impurity.
step 16: the manufacturing step 16 of cylindrical ingot 34
In typically used of the present invention, a kind of intermediates ingot casting 34 that namely method according to the present invention generates preferably has the weight of the diameter 32 of 450 ~ 1100mm, the length 30 up to 6 meters and 400 ~ 30000kg, sees Fig. 3.The manufacture method of ingot casting 34 of the present invention relates to the technology using during the manufacture of ingot casting 34 and can realize cooling fast.Such as, ingot casting 34 forms technology generation by different ingot castings.Suitable manufacturing technology is can be controlled to obtain and to maintain the technology of specific minimum solidification rate.
According to embodiments of the invention, during formation ingot casting, being controlled by average solidification rate is on surface higher than 15 DEG C/min, and at core preferably also higher than 10 DEG C/min.Preferably, while such as can be the freezing range controlled cooling model ingot material of 1400 DEG C ~ 1200 DEG C, this solidification rate is maintained.In other embodiments of the present invention, in this freezing range, being controlled by average solidification rate in working lining is higher than 35 DEG C/min.
From practical point of view, be generally difficult to obtain very high solidification rate when implementing of the present invention.Some embodiments more of the present invention are included in working lining and core and average solidification rate are controlled is 15 DEG C/min ~ 55 DEG C/min or 35 DEG C/min ~ 55 DEG C/min or 45 DEG C/min ~ 55 DEG C/min.
Be such as dissimilar electroflux refining furnace (ESR) for controlling the technology of the technique relevant with Solidification Parameters of the present invention in the present invention, such as, move mould ESR melting or ESR is coated or spray forming technology etc.
The ingot casting using the solidification rate described in the above-mentioned any 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 macrosegregation in the intermediate layer
-there is no secondary segregation
In addition, the ingot casting using technique of the present invention to make has the following advantages to rolled products:
-eliminate " orange peel " effect (outward appearance of the dendrite pattern that it is formed by the wearing and tearing difference of interdendritic regions is formed)
-there is no pin hole problems
-very bright surface smoothness (finish)
-the homogeneity of surface tissue that obtained by surface working
-there is not the 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 Fig. 4 asked for an interview by schematic diagram.
Electroflux refining furnace (ESR) can carry out melting with about 300 ~ 1100kg/h, and comprises electrode holder 36, thrusts portion 38, electrode 40, cooling jacket outlet 42, obtains the cooling jacket entrance 50 of water coolant.In ESR, ingot casting is formed by smelting electrode 40, in ingot material 48, therefore forms different layers, such as, be positioned at molten slag bath 44 and the pool of molten metal 46 of ate electrode.
ESR also comprises the start-up plate 52 by water-cooled 54, sees Fig. 4.The initial ingot casting (electrode 40) that ESR technology may need remelting to be obtained by conventional melting technology, to form ingot casting 48 of the present invention.The careful remelting controlling to use ESR to carry out, to obtain the average solidification rate according to the embodiment of the present invention, such as, average solidification rate higher than 15 DEG C/min in working lining and core between ingot casting Formation period.
Therefore, electrode 40 is heated by an electric current such as high current in ESR technique, with the steel of resmelting electrode, thus forms ingot casting of the present invention.The high current of careful control electrode 40, to control remelt speed, this also affects speed of cooling, thus affects solidification rate.Solidification rate depends on the ampere electric current being supplied to electrode according to predefined function (function).Substantially, ampere electric current is higher, and supply carrys out the power higher (see Ohm's law) of resmelting electrode 40.The power of supply is higher, then slag temperature is higher, and solidification rate is lower.
By maintaining correct remelting rate and slag temperature, in working lining and core, directional freeze can be obtained with solidification rate of the present invention, in certain interval, cooling ingot casting simultaneously.Such as, in one embodiment, in the working lining and core of ingot casting, solidification rate is average all higher than 15 DEG C/min, cools ingot casting in the freezing range of 1400 DEG C ~ 1200 DEG C simultaneously.
According to the present invention, the result that technique and composition of steel as the innovation concept combine, the eutectic carbides content in ingot casting is retained as lower than 5% volume percent.This makes gained roller obtain good grindability index.The grindability index of roller is important, because between the usage period of final roller, grinding obtains the important step for the abundant roughness of the roller of cold-rolling process.It is known that the concentration of 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 trend of dust between the working life of roller in milling train (mill) low.Under contrast, may occur to form dust in the roller that carbide concentration is high, this is disadvantageous to the Working environment in rolled products and milling train.
When manufacturing ingot casting from the composition comprising high-caliber Cr (such as 7 ~ 13%), control solidi fication speed is even more important.The high segregation obtained when solidification rate is crossed slow makes high chromium ingot casting produce defect.
Solidification rate higher than 15 DEG C/min in freezing range during manufacture ingot casting gives low segregation rate, thus obtains the eutectic carbides content lower than 5% volume percent.
The present invention will be easier to understand by reference to following example.But these examples are intended to the modification of the embodiment that ingot casting forming step of the present invention is described, should not be construed as is for limiting the scope of the invention.
comparative example
Example 1 illustrates the impact of method of the present invention on the microstructure of roller 1 of the present invention.Example 2 is comparative examples.These examples were carried out in production full scale roller sample (prototype) period.Experiment shows that the distribution of the eutectic carbides cast in rear ingot casting and network shape are according to the solidification rate generation important change used, and see example 1,2 and the table 2 of below.The network shape seen in ingot casting and being distributed in the final roller after according to forging of the present invention and tempering of eutectic carbides are retained.
example 1
This example illustrate the impact on the microstructure of roller of the present invention when forming the solidification rate used during ingot casting 34 of the present invention higher than 15 DEG C/min.
Fig. 5 A ~ 5B shows to use and is cooled to from 1400 DEG C the example that average solidification rate while 1200 DEG C is the microstructure of the ingot casting of the present invention 1 that the technique of 50 DEG C/min (the 90mm depths at ingot casting) is made.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 ingot casting different piece, see Fig. 8, show core 82, middle radius 84,90mm place 86,50mm place 88,30mm place 90 and surface 92 temperature rate.Fig. 5 B is the enlarged view of Fig. 5 A.Separately in table 2.
Fig. 6 A ~ 6B shows to use and is cooled to from 1400 DEG C the example that average solidification rate while 1200 DEG C is the microstructure of the ingot casting of the present invention 2 that the technique of 18 DEG C/min (the 90mm depths at ingot casting) is made.Fig. 6 A and 6B shows the eutectic cell in example ingot casting 2 of the present invention, and they are little, sees such as cross-sectional distance 1024.For the different freezing ranges 80 of solidificating period in ingot casting different piece, see Fig. 9, show core 100, middle radius 102,90mm place 104,50mm place 106,30mm place 108 and surface 110 temperature rate.Fig. 6 B is the enlarged view of Fig. 6 A.Separately in table 2.
conclusion
Method of the present invention guarantees to there is not segregation at the middle radius of ingot casting.There is not segregation at middle radius (or 5/6 of the inboard portion of the diameter of cylindrical roller) and ensure that the integrity of roller during hardening process.Therefore, generate thinner microstructure higher than the solidification rate of 15 DEG C/min in working lining, it is bright as noted earlier, better with regard to grinding and dust pollution, sees Fig. 5 A ~ 5B and Fig. 6 A ~ 6B.
example 2
This example illustrate the effect using the solidification rate lower than 15 DEG C/min between test 1 ingot casting Formation period.
Fig. 7 A ~ 7C shows the example of the microstructure at test 1 ingot casting made lower than the technique of 15 (in fact even lower than 10) DEG C/min with solidification rate while the freezing range of 1400 DEG C to 1200 DEG C cooling ingot casting.Colony 700 size for test 1 ingot casting compared shown in Fig. 7 A ~ 7C is comparatively large, and see such as cross section 708, it has the cross-sectional length 708 of the maximum cross-section of the ingot casting 1 be greater than in such as example 1 of the present invention.Test 1 ingot casting and also present shrinkage porosite 704.Thick polymerization eutectic net 702 also can be seen in Fig. 7 A ~ 7C.Separately in table 2.Fig. 7 B ~ 7C is the enlarged view of Fig. 7 A.
conclusion:
Cause the middle radius place carbide of test 1 ingot structure and the high segregation of thick carbide network 702 and shrinkage porosite 704 lower than the solidification rate of 15 DEG C/min in freezing range, see Fig. 7 A ~ 7C.The high segregation of thick carbide network and carbide makes the openpore roller (whiteblankroll) made according to the ingot casting of test 1 or final roller become fragile, and is therefore easy to blast in induction hardening (openpore roller) or cold rolling processing (final roller) period.
It is thick that example 2 solidification rate that also show lower than 15 DEG C/min also makes the size of eutectic cell structure than when being made ingot casting by the solidification rate higher than 15 DEG C/min according to the present invention.
Solidification rate higher than 15 DEG C/min in freezing range during manufacture ingot casting gives low segregation rate, thus obtains the eutectic carbides content lower than 5% volume percent.
Table 2
Table 2 shows the experimental data of testing ingot casting while the 90mm depths of ingot casting cools ingot casting from 1400 DEG C to 1200 DEG C with the average solidification rate of difference (*).
comparative example
Example 3 is for illustration of the impact of chemical composition on the microstructure of ingot casting thus on roller of the present invention of such as method of the present invention and ingot casting.Example 4 is comparative examples.Example 3 and 4 shows the microstructure of carrying out testing the ingot casting generated in the lab with controlled freezing device and controlled speed of cooling.
The impact of the chemical composition that the shape of eutectic carbides net is used in ingot casting, separately in table 3.
example 3
This example illustrate the microstructure of carrying out testing generated ingot casting 1 according to method of the present invention in the lab with the controlled speed of cooling higher than 15 DEG C/min in controlled freezing device and freezing range.When used according to the invention comprise the chemical composition of 1.4%Mo time, in ingot structure, obtain open eutectic carbides system 750, see Figure 10 A ~ 10B.Separately in table 3.This opening eutectic carbides system 750 observed in roller 1 according to the present invention is characterized by dendrite pattern, and Microstructures of Eutectic Carbides 752 does not form closed eutectic carbides net (such in such as comparative example 4, test 2), but form dendritic arm in a network, see Figure 10 A ~ 10B, it illustrates the microstructure picture of the ingot casting containing 1.4%Mo according to Process Production of the present invention.This opening eutectic carbides system of the present invention makes roller than the roller made of Mo using content higher than 1.6% and easily to grind.
example 4
Testing 2 ingot castings uses technique of the present invention to make, and in its composition, main ingredient is corresponding to above-described embodiment, but difference is chemical composition in the content of Mo, be different from the present invention.This test 2 ingot casting carries out testing generated in the lab with the controlled speed of cooling higher than 15 DEG C/min in controlled freezing device and freezing range according to method of the present invention.In test 2, the content of Mo is 2.77%, separately in table 3.In technique of the present invention, use the chemical composition comprising the Mo of 2.77% to generate ingot casting makes the eutectic carbides system of ingot casting be configured as closed eutectic carbides colony, see Figure 11 A ~ 11B, and eutectic carbides 852 forms the part 850 of basic isolation, as illustrate test 2 microstructure Figure 11 A ~ 11B in isolated or be separated colony structure.White area in Figure 11 A ~ B represents matrix, mainly iron, and black area is time level carbide.
The excessive interpolation testing 2 interalloy elements causes forming thick carbide network, is linked to the segregation of carbide.Separately in table 3.
Table 3
Test the experimental data of ingot casting with the average solidification rate of difference (*) while table 3 shows and cools ingot casting from 1400 DEG C to 1200 DEG C.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, carry out forge hot pressure to ingot casting 34, method is the known technique of use itself, makes them by between forging hammer and hammer anvil, reduces section area simultaneously and changes shape, ingot casting to be formed as roller 1 of the present invention.In special furnace, heat ingot casting, see that Figure 12 is to watch the schematic diagram of forging step.
Forging step 18 according to the present invention comprises the following steps, and sees Figure 12:
Preheat 56 ingot castings 34 and reach about 6h, to the temperature of 800 ~ 1200 DEG C or 850 ~ 1100 DEG C.Preheating steps 56 relates to from surface heating ingot casting 34 until the core of ingot casting.Temperature temperature during forging regulated in the interval of 800 ~ 1200 DEG C or 850 ~ 1100 DEG C, because can cause ingot structure, because of the burning of roller, defect occurs higher than 1200 DEG C.The reason temperature of ingot casting being remained on pointed temperature range ingot casting can be caused to form crackle lower than the temperature of 800 DEG C.Along with ingot casting 34 cools, its intensity uprises, ductility step-down, if continue distortion, then may cause cracking.
After the preheating (step 56) of ingot casting 1, the forging ratio of 1.35 ~ 2.0 is used to carry out forging (step 60).Repeat forging step 60 and pre-heating step 56, this forging cycle is commonly referred to as a heat (heat) 58.Repeat heat 58 by desired times, 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 so a kind of roller, and it has the shape of roller but roll body also lacks and finally processes to become the roller that can use in milling train.
In another embodiment, ingot casting 34, by the some heats 58 of forging, is shown in that Figure 13 is to watch the schematic diagram of forged roll:
A) first, in several or 1 ~ 2 heat 58, the section area of ingot casting 34 is regulated,
B) in a heat, make a neck of roller,
C) in next heat, forge another neck of roller.
Forge that composition of steel of the present invention is more difficult to carry out, because compared with the Standard Steel trade mark of forging example, alloy content of the present invention is high.
During forging, ingot casting 34 diameter 32 while being forged into roller 1 of the present invention reduces 30 ~ 50%.Such as, 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 formed during coagulation step 80 in the manufacturing processed of ingot casting 34.What show is can use hot forging technology to forge to have eutectic carbides microstructure of the present invention, eutectic carbides content lower than the ingot casting 34 of 5% volume percent.Using such as can make these big rollers set off an explosion during induction hardening or in milling train with the ingot casting formed lower than the solidification rate of 15 DEG C/min with other technique.
step 20: preliminary thermal treatment is carried out to described roller 1
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 DEG C ~ 1100 DEG C during preliminary thermal treatment 20 of the present invention in a stove, then remains on this temperature and reaches certain hour, until there occurs gratifying hydrogen trap.Carrying out preliminary thermal treatment (normalizing and Spheroidizing Annealing) is workability in order to improve roller.
step 22: roughing 22 is carried out to described roller
In manufacturing process of the present invention, by roughing step 22 treatment tube.Roughing 22 is carried out to roller 1 formed according to the present invention and refers to the skin removing forged roll.In one embodiment of the invention, skin is removed during roughing.Roller is referred to as black base (blackblank) before roughing process.By removing roller zone of oxidation on the surface, so black base roller is transformed into openpore.
step 24: induction hardening is carried out to described roller 1
In manufacturing process of the present invention, carry out 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 induction hardening step, downward slowly mobile roller while the electric voltage frequency being applied 50 ~ 1000Hz by inductor assembly 70 or electric current.After the heating step, use water-cooled 72 cooling roller 1, see Figure 14.The hard surface formed, also referred to as the working lining 4 of roller, is about 1/6 (see Fig. 1, label 6) of the whole diameter 2 of roller 1.Roller face is rapidly heated when being dropped through a series of inductor block comprising the wire loop of guiding in quench box.The Rapid Thermal of induction heating is permeated and is and then used the chilling of water to form the predetermined layer with uniform rigidity at roll surface.The neck of roller and core remain on low temperature in whole process.During induction hardening, the frequency that the surface to roller 1 applies is generally 50 ~ 1000Hz, and gives the darker working lining of roller 14 from this interval compared with the frequency selected lower part.The other factors affecting the degree of depth of the working lining formed has the gap of (if employing multiple inductor block) 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 be once, twice or more time.
Roller of the present invention is blasted when using Traditional hardening technology, and induction heating is the most proper technology for the roller of the present invention that hardens.During induction hardening 24, the cooling of pair roller 1 is undertaken by the cold water of large discharge.
In one embodiment of the invention, induction hardening 34 has been come by twice induction hardening, and after induction hardening 24, the cooling of pair roller 1 is 40 DEG C by temperature and feed flow is about 300m 3the large discharge water of/h has come, and roller moves down with the speed of 0.3 ~ 1mm/s.
In one embodiment, induction hardening step 24 0.5 ~ 2h consuming time.
step 26: tempering is carried out to described roller
In manufacturing process of the present invention, pair roller 1 carries out tempering.The object of tempering step is the fragility reducing roller, and regulates firmness level.Tempering step 26 is the committed steps during roller is formed, because it reduces internal stress.During tempering step, roller obtains the secondary precipitation of final microtexture and carbide by spreading.Air cooling is applied between tempering heating steps.Preferably carry out 3 tempering at 450 ~ 530 DEG C of pair rollers.Tempering step make roller obtain higher than 780HV or needed for 780 ~ 840HV firmness level.Very crucial to the accurate control of temperature and time during tempering process, to obtain the very balanced microstructure such as such as tempered martensite, the roller that technique according to the present invention is made comprises austenite after tempering and remains than the tempered martensite lower than 5% volume percent.
step 28: described roller is processed
In manufacturing process of the present invention, preferably processed by procedure of processing 28 pair roller before for milling train.Such as, at milling train, carry out pair roller by process of surface treatment such as grindings and carry out applying specific surface treatment, to obtain the roughness of expectation and relevant friction on the surface of roller.The surface-treated example of pair roller such as has: laser beam surface processing (LBT), electron beam surface processing (EBT) or electric discharge surface processing (EDT).
In one embodiment, treatment tube is carried out 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 comprising low chromium component.Figure 15 C ~ 15D shows the surface microhardness of roller of the present invention after electric discharge surface processing.Below white 300 in Figure 15 D, there is again the layer of austenitizing and thinner softened region, because this trade mark has high tempering temperature.Also it is noted that in the white of Figure 15 D, eutectic carbides 302 is not by the impact of arc energy.For comparing, the carbide of these classifications does not exist in the roller shown in Figure 15 A ~ B.Roller of the present invention has better character and performance, because there is hard eutectic carbides in white than standard brand roller (see Figure 15 A ~ 15B).
Figure 18 shows more schematically scheming of Figure 15 D, shows the microstructure of roll surface of the present invention, in white 304, wherein there is the eutectic carbides 302 newly formed because of remelting.In addition, also show the eutectic carbides 300 previously formed in Figure 18.Roll surface in Figure 18 shows and how seems according to the surface after the present invention carries out electric discharge surface processing.Graduated scale 306 represents 5 μm.
The roller 1 made by above-mentioned technique of the present invention
The diameter of typical roller of the present invention is 215 ~ 800mm or 250 ~ 700mm, and comprise the whole length of neck up to 6 meters, wherein barrel lenght is 1 ~ 3 meter.The typical weight of roller is 400 ~ 10000kg.The feature of the microstructure of the roller of one embodiment of the invention is that comprising austenite remains than the tempered martensite lower than 5% volume percent, and its central roll comprises the open eutectic carbides net being less than 5% volume percent eutectic carbides; And roller 1 presents the hardness of 780 ~ 840HV; With-300 to the internal compression stresses of-500MPa.These character of roller are the chemical compositions due to roller production technique of the present invention and the roller according to chemical composition of the present invention.
Roller of the present invention is intended to the cold-strip mill of the roller that can bear high pressure for demand.Roller intention of the present invention is used as working roll in cold-strip mill, and any frame (stand) be applicable in rolling technology, and be applicable to 2Hi ~ 6Hi milling train, and the roughness of 0.3 ~ 0.5 μm of demand in finishing stand, the roughness of 1.5 ~ 2.5 μm to demand in pony roughing mill can be had from the teeth outwards.
The present invention will be easier to understand by reference to following example.But these examples are intended to the character that roller of the present invention is described, and to should not be construed as be for limiting the scope of the invention.
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 freezing range in working lining higher than 15 DEG C/min, and the induction heating frequency used is 50 ~ 250HZ, and carries out 3 tempering at 450 ~ 530 DEG C.
Roller of the present invention 2 in table 4 uses technique of the present invention to make, the solidification rate used is 18 DEG C/min in freezing range in working lining, and the induction heating frequency used is 50 ~ 250HZ, and carry out 3 tempering, first time 490 DEG C carry out, then 490 DEG C carry out, last tempering carries out at 480 DEG C.Figure 19 A and 19B shows 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 there is the microstructure 1034 of open eutectic net.
Table 4
The Mn content of table 4 central roll is all in the scope of 0.4 ~ 0.5, and the Si content of table 4 central roll is all in the scope of 0.2 ~ 2.0, and Ni is always lower than 1%.
the application of roller
The application that roller is suitable for has:
Aluminum i ndustry:
The irreversible milling train of-single chassis 4Hi
Steel industry:
-4Hi single chassis is reversible
-4Hi tandem 4 and 5 frame, for the sheet material in continuous and discontinuous technique
-4Hi tandem 4 and 5 frame, for tin plate
-6Hi tandem mill, for sheet material
roller purposes
Forged roll of the present invention is suitable for use as working roll in such as cold-rolling mill or intermediate roll or such as:
-for the rolled thickness reduction milling train of the reversible and irreversible frame of tin plate, sheet material, silicon steel, aluminium or copper, roughing and finishing stand.
-cold rolling tempering and/or skin-pass milling train;
-be configured to have the milling train of two rollers (High) on processed or untreated surface, four rollers and six roller frames.
-AHSS (AdvancedHighStrengthSteel, AHSS) grade of steel cold rolling.
roll surface
Surface tissue
A problem of existing roller is that surface tissue weares and teares between the usage period of roller.Surface tissue is important, because it guarantees frictional coefficient, to avoid skidding and/or the 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 of roller, wherein white comprises as M 7c 3hard eutectic carbides.In working lining, the microstructure of roller of the present invention after finished heat treatment by austenite remain than lower than 5% volume percent tempered martensite and slightly and be evenly distributed in matrix as MC and M 2the carbide of C (M=metal, C=carbon) is formed.This microstructure has shown the surface tissue of maintaining roller very important.
Roughness shifts
Roughness transfer (roughnesstransfer) of roll surface 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 be due to special requirement composition and manufacture roller time the production method that uses.
Free program rolling in milling train
A problem during roller is used to be that the dirt accumulated on roll surface leaves trajectory on band.In working lining, roller of the present invention has strong surface because the microstructure of roller of the present invention comprise austenite remain than lower than 5% volume percent tempered martensite 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 possibility of free program rolling.
Scaling
Another problem of existing roller is that the cumulative stress of the propagation of crackle in roller caused by the region of the residualinternal stress of roller and mill operation is arranged.Roller in using is subject to a complex set of stress.Roller of the present invention demonstrates low-level residualinternal stress, therefore resists scaling (spalling) better, and this makes milling train casualty ratio of accidents step-down.
The physical strength of the roller of the present invention but roller that production method different identical from roller of the present invention than alloying constituent good.The physical strength of roller of the present invention is the open eutectic net owing to being formed in the working lining of roller.This opening eutectic net is formed in the cooling step in roller manufacturing process.The formation of solidification rate to the open network be present in roller of the present invention higher than 15 DEG C/min during manufacture ingot casting in cooling step is most important.
In addition, the accumulation of each temper of carrying out at the high temperature of production period after the sclerosis of such as 450 ~ 530 DEG C of roller causes the important lax of the internal stress 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 inwardly to be measured between 20 ~ 120mm diametrically from roll surface.The internal compression stresses of roller of the present invention is preferably between-300 to-500MPa or such as lower than-400MPa on absolute value.
the microstructure of roller
Figure 17 A shows the schematic diagram of the present invention one example roller microstructure.Dendritic arm 210 can being seen in Figure 17 A, be made up of eutectic carbides, forming eutectic cell structure 204 by forming open carbide network.In Figure 17 A, the open eutectic net be made up of dendritic arm 210 of appreciable formation eutectic cell 204 is formed in process because of peculiar chemical composition of the present invention.Graduated scale 208 represents 100 μm.
In one embodiment of the invention, the microstructure of roller of the present invention comprises only a covering crystal grain of colony structure or the open eutectic net of two crystal grain.
By contrast, Figure 17 B shows closed eutectic net, and wherein eutectic carbides 200 forms the closed eutectic net that eutectic cell 212 is obviously separated.This net is undesired in roller of the present invention, because if roller contains this microstructure, then can become fragile.Graduated scale 214 represents 100 μm.
The present invention is described above by the different embodiments be in the scope of claims.

Claims (49)

1. the roller (1) of a forging, comprise a kind of composition of steel, this composition of steel comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than (>) 1.0 and be less than or equal to 3.0% V,
Remainder mainly Fe and trace and/or the inevitable impurity of steel;
The microstructure of wherein said roller (1) comprising:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of-eutectic carbides is less than (<) 5% volume;
And wherein said roller (1) presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
2. the roller as described in the claims, wherein, described open eutectic carbides net defines the eutectic cell of colony shape apperance.
3. the roller according to any one of the claims, wherein, described open eutectic carbides net comprises dendritic arm.
4. roller as claimed in claim 1, wherein, described microstructure is at least present in the working lining of described roller.
5. roller as claimed in claim 1, its composition of steel is composed as follows with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than (>) 1.0 and be less than or equal to 3.0% V,
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the Ni of (<) 1%
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2
Be less than the W of (<) 2%, and
Be less than the Nb of (<) 1%, and
Be less than the Ti of (<) 1%, and
Be less than the Ta of (<) 0.5%, and
Be less than the Zr of (<) 0.5%,
Remainder mainly Fe and trace and/or the inevitable impurity of steel.
6. roller as claimed in claim 1, 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 claimed in claim 1, 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 claimed in claim 1, 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 claimed in claim 1, 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 claimed in claim 1, wherein, the Si content in described composition of steel account for regard to weight percent whole roller heavy 0.85 ~ 1.15%.
11. rollers as claimed in claim 1, wherein, the Cr content in described composition of steel account for regard to weight percent whole roller heavy 7.0 ~ 11%.
12. rollers as claimed in claim 1, wherein, the Cr content in described composition of steel account for regard to weight percent whole roller heavy 7.3 ~ be less than (<) 8.0%.
13. rollers as claimed in claim 1, wherein, the Mo content in described composition of steel account for regard to weight percent whole roller heavy 1.45 ~ 1.55%.
14. rollers as claimed in claim 1, wherein, the Ni content in described composition of steel account for regard to weight percent whole roller heavy be less than (<) 0.3.
15. rollers as claimed in claim 1, wherein, the V content in described composition of steel account for regard to weight percent whole roller heavy 1.3 ~ 2.1%.
16. rollers as claimed in claim 1, wherein, the V content in described composition of steel account for regard to weight percent whole roller heavy 1.3 ~ 1.6%.
17. rollers as claimed in claim 1, wherein, described composition of steel component with regard to weight percent is as follows:
The C of 0.8 ~ 0.99%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.2 ~ 1.5%, and
The Cr of 7.0 ~ 11%, and
The Mo of 0.6 ~ 1.6%, and
Be less than the Ni of (<) 1.0, and
The V of 1.0 ~ 2.1%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
Remainder mainly Fe and trace and/or the inevitable impurity of roller.
18. rollers as claimed in claim 1, wherein, described composition of steel component with regard to weight percent is as follows:
The C of 0.85 ~ 0.9%, and
The Mn of 0.4 ~ 0.5%, and
The Si of 0.85 ~ 1.15%, and
7.3 ~ be less than the Cr of (<) 8.0%, and
The Mo of 1.45 ~ 1.55%, and
Be less than the Ni of (<) 0.3, and
The V of 1.3 ~ 1.6%, and
Be less than the P of (<) 0.015%, and
Be less than the S of (<) 0.015%, and
Be less than the O of (<) 30ppm 2, and
Be less than the N of (<) 100ppm 2, and
Be less than the H of (<) 3ppm 2, and
Remainder mainly Fe and trace and/or the inevitable impurity of roller.
19. rollers as claimed in claim 1, be structured as further cold rolling in working roll.
20. rollers as claimed in claim 1, have the weight being greater than 400kg further.
21. rollers as claimed in claim 1, have the diameter within the scope of 215 ~ 800mm further.
22. rollers as claimed in claim 1, wherein said roller is without coating.
23. rollers as claimed in claim 1, wherein said roller coat is covered with optional coating.
24. rollers as claimed in claim 23, wherein said coating is chromiumcoating.
25. 1 kinds, for the manufacture of the technique of roller, comprise the following steps:
A. provide a kind of composition of steel, it comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than (>) 1.0 and be less than or equal to 3.0% V,
Remainder mainly Fe and trace and/or the inevitable impurity of steel;
B. manufacture ingot casting, in freezing range, in the working lining of ingot casting, maintain the solidification rate higher than 15 DEG C/min;
C. this ingot casting is forged into roller;
D. by induction heating, roller is hardened;
E. with the temperature of 450 ~ 530 DEG C, tempering is carried out to reach the hardness of 780 ~ 840HV to described roller;
Thus obtain the microstructure of described roller (1), it comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And wherein said roller (1) presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
26. techniques as claimed in claim 25, wherein, maintain 15 DEG C/min ~ 55 DEG C/min to manufacture ingot casting by the solidification rate of working lining and core.
27. techniques as claimed in claim 26, wherein, maintain 17 DEG C/min ~ 50 DEG C/min to manufacture ingot casting by the solidification rate of working lining and core.
28. techniques as claimed in claim 26, wherein, maintain 35 DEG C/min ~ 55 DEG C/min to manufacture ingot casting by the solidification rate of working lining and core.
29. techniques as claimed in claim 26, wherein, maintain 45 DEG C/min ~ 55 DEG C/min to manufacture ingot casting by the solidification rate of working lining and core.
30. techniques according to any one of claim 25-26, wherein, maintain the solidification rate higher than 35 DEG C/min, manufacture ingot casting in the working lining of freezing range at ingot casting.
31. techniques as claimed in claim 25, wherein, for described ingot casting, described freezing range is 1400 ~ 1200 DEG C.
32. techniques as claimed in claim 25, wherein, control ampere electric current source by the predefined function according to solidification rate, maintain the solidification rate selected in advance in electroflux refining furnace technical matters, thus manufacture ingot casting.
33. techniques as claimed in claim 25, wherein, step ingot casting being forged into roller comprises the following steps:
A. ingot casting is heated to 800 ~ 1200 DEG C, preferably continues 6 hours;
B. described ingot casting is forged in the temperature higher than 800 DEG C;
C. repeating step a ~ b, until described ingot casting is formed as the roller with intended shape and size.
34. techniques as claimed in claim 33, wherein, are heated to 850 ~ 1100 DEG C by ingot casting.
35. techniques as claimed in claim 25, after forging step, also comprise preliminary heat treated step, the temperature of preferably to 700 ~ 1100 DEG C, comprises hydrogen trap process.
36. techniques as claimed in claim 35, the temperature of described preliminary heat treated step preferably to 800 ~ 900 DEG C.
37. techniques as claimed in claim 25, wherein, the step that pair roller carries out tempering comprises the following steps:
A. described roller to 450 ~ 530 DEG C are heated, preferably 3 times,
B. between each heating steps, air cooling is carried out to described roller.
38. techniques as claimed in claim 25, also comprise and carry out mechanical workout to described roller, to process the white comprising eutectic carbides.
39. techniques as claimed in claim 38, wherein, the eutectic carbides in described white is from M 7c 3in to select.
40. techniques as claimed in claim 25, also comprise the feature any one of claim 1-21.
41. techniques as claimed in claim 25, wherein said roller is without coating.
42. techniques as claimed in claim 25, wherein said roller coat is covered with optional coating.
43. techniques as claimed in claim 42, wherein said coating is chromiumcoating.
The roller (1) of 44. 1 kinds of forgings, the Process Production by comprising the following steps:
A. provide a kind of composition of steel, it comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than (>) 1.0 and be less than or equal to 3.0% V,
Remainder mainly Fe and trace and/or the inevitable impurity of steel;
B. manufacture ingot casting, in freezing range, in the working lining of ingot casting, maintain the solidification rate higher than 15 DEG C/min;
C. this ingot casting is forged into roller;
D. by induction heating, roller is hardened;
E. pair roller carries out tempering;
Thus obtain the microstructure of described roller (1), it comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<);
And wherein said roller (1) presents:
The hardness of-780 ~ 840HV; With
--the internal compression stresses of 300 to-500MPa.
45. rollers as claimed in claim 44, also comprise the feature any one of claim 1-32.
46. rollers as claimed in claim 44, wherein said roller is without coating.
47. rollers as claimed in claim 44, wherein said roller coat is covered with optional coating.
48. rollers as claimed in claim 47, wherein said coating is chromiumcoating.
Intermediates ingot casting in the production process of 49. 1 kinds of rollers according to any one of the claims 1-24 and 44-48, comprises a kind of composition of steel, and this composition of steel comprises with regard to weight percent:
0.8 to the C being less than (<) 1%,
The Mn of 0.2 ~ 0.5%,
The Si of 0.2 ~ 2.0%,
The Cr of 7.0 ~ 13.0%,
The Mo of 0.6 ~ 1.6%,
Be greater than (>) 1.0 and be less than or equal to 3.0% V,
Remainder mainly Fe and trace and/or the inevitable impurity of steel;
And the microstructure of the final roller wherein made from described ingot casting comprises:
-austenite is residual than being less than (<) 5% tempered martensite of volume percent; With
The open eutectic carbides net of 5% volume percent that-eutectic carbides is less than (<).
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