CN106435132B - A kind of processing method of low-carbon alloy steel - Google Patents
A kind of processing method of low-carbon alloy steel Download PDFInfo
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- CN106435132B CN106435132B CN201610948889.5A CN201610948889A CN106435132B CN 106435132 B CN106435132 B CN 106435132B CN 201610948889 A CN201610948889 A CN 201610948889A CN 106435132 B CN106435132 B CN 106435132B
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
Abstract
A kind of processing method of low-carbon alloy steel of the present invention, comprises the following steps：A) low-carbon alloy steel billet is cast, the low-carbon alloy steel billet is forged to slab；B) slab is subjected to hot rolling, obtains finish to gauge plate；C) the finish to gauge plate is warming up to after coexistence region temperature and deformed immediately, water quenching is to room temperature after isothermal holding.Method combination low-carbon alloy steel coexistence region provided by the invention keeps the temperature the behavior of alloying element partition, coexistence region thermal deformation produces the effect that the realization such as room and interstitial atom promotes alloying element partition, intrinsic alloys producing in steel is not only played, and on the basis of original C partitions are given full play to, improve aggregation extent of the alloying element in austenite (room temperature martensite), to stablize more retained austenites in follow-up Q＆P treatment process, making up the strength and ductility product that low-carbon is brought reduces offer beneficial support.Test result indicates that the present invention can make the enrichment degree of alloying element improve 2%~5%.
Description
Technical field
The invention belongs to metal working technical area, more particularly to a kind of processing method of low-carbon alloy steel.
Background technology
Q＆P processing steel is mostly C-Si-Mn systems steel, and generally in 0.2~0.6 (mass fraction, %), higher carbon contains carbon content
Amount not only improves intensity, can also strengthen partition effect, plays the role of improving strength and ductility product, but C content is excessive can also increase steel
Quenching degree, increase heat affected area in welding and cause weld cracking, reduce welding performance, increase the cold brittleness and timeliness of steel
Sensitiveness.Therefore, the carbon content as automobile steel is usually no more than 0.2%；But carbon content again cannot be too low, carbon otherwise will be made
Partition effect is subject to a definite limitation, and remained austenite content is reduced after on the one hand making quenching, is unfavorable for plasticity raising；On the other hand make
Carbon content is reduced in lath martensite, reduces lath martensite intensity.In order to solve this contradiction, research is found that alloying element
Mn partitions are also to regulate and control a kind of effective means of remained austenite content, and when being annealed in critical zone, manganese element is to austenite
The result of study that the stability of diffusion couple raising austenite plays certain effect, Seawoong Lee etc. also indicates that manganese is first
Element can be enriched with when coexistence region is annealed to austenite medium or short range, improve the stability of austenite.Therefore, Mn elements can be utilized
The behavior being enriched with coexistence region into austenite, and Q＆P process is carried out to mild steel, reach and stablize more retained austenites
The effect of body, but manganese is displaced type element, and it is very slow in the speed of Ovshinsky vivo migration and diffusivity is limited, under finally stablizing
The Ovshinsky scale of construction come is also seldom.
H.P.Liu et al., using new drop stamping and quenching-match somebody with somebody division technique, introduces austenite on Q＆P Process ba- sis
Hot compression deformation obtains fine grain austenite, and the irregular martensite of broken refinement, scattered geneva can be obtained after quenching partition
Body plate and film-form, high density dislocation density phase transformation strengthening retained austenite, by the high density dislocation in martensite with
The intensity of martensite is improved, so as to improve the intensity and elongation of steel, reaches strength and ductility product best of breed.Pass through thermal deformation technique
Crystal grain has not only been refined, but also has added dislocation and vacancy concentration, there is provided elements diffusion passage, for the more residual austenites of stabilization
The scale of construction provides possibility.But the strength and ductility product of the steel of this method acquisition needs to further improve.
The content of the invention
In view of this, it is an object of the invention to provide a kind of processing method of low-carbon alloy steel, side provided by the invention
Low-carbon alloy steel after method processing can promote alloying element partition, so as to further improve its strength and ductility product.
A kind of processing method of low-carbon alloy steel of the present invention, comprises the following steps：
A) low-carbon alloy steel billet is cast, the low-carbon alloy steel billet is forged to slab；
B) slab is subjected to hot rolling, obtains finish to gauge plate；
C) the finish to gauge plate is warming up to after coexistence region temperature and deformed immediately, water quenching is to room temperature after isothermal holding.
Method combination low-carbon alloy steel coexistence region provided by the invention keeps the temperature the behavior of alloying element partition, coexistence region thermal deformation
The effect that the realization such as room and interstitial atom promotes alloying element partition is produced, has not only played the work of intrinsic alloying element in steel
With, and on the basis of original C partitions are given full play to, improve aggregation journey of the alloying element in austenite (room temperature martensite)
Degree, is to stablize more retained austenites in follow-up Q＆P treatment process, and making up the strength and ductility product that low-carbon is brought reduces the favourable branch of offer
Support.Test result indicates that of the present invention deform the method for promoting alloying element partition using coexistence region, alloying element can be made
Enrichment degree improves 2%~5%.
The present invention casts low-carbon alloy steel steel billet first, is then forged to slab.Specifically, the low-carbon alloy
Steel can be low-carbon silico-manganese steel.In one embodiment, the composition of low-carbon alloy steel is：The C of 0.18wt%；1.58wt%'s
Si；The Mn of 2.06wt%；The Cu of 0.41wt%；The Ni of 0.33wt%；The P of 0.008wt%；The S of 0.005wt%；
The B of 0.0017wt%；The Fe of surplus.In another embodiment, the composition of low-carbon alloy steel is：The C of 0.19wt%；
The Si of 1.5wt%；The Mn of 1.3wt%；The P of 0.010wt%；The Al of 0.017wt%；The S of 0.009wt%；0.0003wt%'s
B；The Fe of surplus.The present invention can smelt steel billet in ZG-50 vacuum induction melting furnaces, be then forged to slab.
After being forged to slab, hot rolling treatment is carried out, obtains finish to gauge plate.Specifically, the slab is existed first
Hot rolling is carried out after 1100~1300 DEG C of 2~4h of isothermal holding, start rolling temperature is 1000~1200 DEG C, through 3 passes postcoolings
To 900~1000 DEG C of 5 passes of process, finish to gauge plate is obtained after turning.In a specific embodiment, the slab is existed
Hot rolling is carried out after 1200 DEG C of isothermal holding 3h, start rolling temperature is 1100 DEG C, through 3 passes postcoolings to 950 DEG C, then by 5
Passes, obtain finish to gauge plate after turning.In another specific embodiment, hot rolling is divided into roughing and is carried out successively with finish rolling, slightly
1100 DEG C of start rolling temperature is rolled, roughing pass deformation is 33%, and finish rolling total deformation is 70%, and finishing temperature is 950 DEG C, finish to gauge
Thickness of slab is 15mm.In a specific embodiment, slab thickness 75mm, hot rolling is carried out after 1200 DEG C of isothermal holding 3h, is opened
Temperature is rolled for 1100 DEG C, through 3 passes to 50mm, is cooled to 950 DEG C, then the heat by 5 passes into thickness for 15mm
Plate is rolled, the finish to gauge plate of Φ 8mm × 12mm is processed into using wire cutting machine tool.
After obtaining finish to gauge plate, deformed immediately after being warming up to coexistence region temperature, water quenching is to room temperature after isothermal holding.Its
In, coexistence region temperature is 740~770 DEG C, is preferably warming up to coexistence region temperature with 5~15 DEG C/s, the speed of more preferably 10 DEG C/s.
After being warming up to coexistence region temperature, deform immediately, the deflection of the deformation is 5%~15%, is preferably 10%, preferably with 1s-1
Rate of deformation deformation.The deformation process is completed on Gleeble3500 thermal simulation machines, during hot compression test,
A pair of of thermocouple of position welding, the feedback signal of the thermocouple is received come the temperature of automatic Control Assay by computer between in the sample
Degree.Isothermal holding is carried out after deformation, the time of the isothermal holding is 600~1800s.
Referring to Fig. 1, Fig. 1 is the heat treatment process schematic diagram of the processing method provided by the present invention, wherein, it is warming up to 740~
600~1800s is kept the temperature after 770 DEG C, and water quenching to room temperature is undeformed processing mode again, is become immediately after being warming up to 740~770 DEG C
Shape 10% keeps the temperature 600~1800s again and then water quenching to room temperature is the processing mode of deformation provided by the invention.
After above-mentioned processing, the low-carbon alloy steel observed, the results showed that, steel is obtained after processing provided by the invention
Yang Zhong room temperature textures are ferrite and martensite (coexistence region austenite) phase.After method provided by the invention processing, C, Mn,
Significant change occurs for distribution of the alloying elements such as Cu in room temperature texture in martensite and ferrite, occurs in martensite obvious
Enrichment, it is not deformed to be compared with EPMA pictures that are deforming, find under identical soaking time, the experiment steel of deformation is in coexistence region
C, Mn, Cu enrichment of element phenomenon occur in advance, and enrichment degree improves, i.e., method provided by the invention can promote element to match somebody with somebody
Point.
The present invention is kept the temperature+deformation-using coexistence region and quenched using the experiment steel that original structure is ferrite and pearlite as raw material
Fiery treatment process, can make tissue produce high density dislocation, room and higher elastic strain energy, abnormal using coexistence region thermal deformation
Become energy, provide diffusion admittance for diffusion of alloy elements, deformation also provides extra driving force for atoms permeating, so as to promote to close
Gold element partition, increase alloying element obtain congregational rate in austenite (room temperature martensite).
The present invention promotes alloying element partition using coexistence region deformation, reaches following purpose：1. deformation can in coexistence region
Produce the point defects such as a large amount of rooms, interstitial atom promote alloying element ferrite (α) mutually with the expansion in austenite (γ) phase
Dissipate；2. deformation can promote alloying element by ferrite (α) mutually to the partition behavior in austenite (γ) phase in coexistence region, it is closed
Gold element partition effect is more preferable, enrichment of element degree higher.
Brief description of the drawings
Fig. 1 is the heat treatment process schematic diagram of the processing method provided by the present invention；
Fig. 2 is the room temperature texture SEM figures for the steel that the embodiment of the present invention 1 obtains；
Fig. 3 is the room temperature texture SEM figures for the steel that comparative example 1 of the present invention obtains；
Fig. 4 is the micro-organization chart of room temperature texture for the steel that the embodiment of the present invention 1 obtains；
Fig. 5 is the EPMA figures that C element is distributed in the steel room temperature texture that the embodiment of the present invention 1 obtains；
Fig. 6 is the EPMA figures of Mn Elemental redistributions in the steel room temperature texture that the embodiment of the present invention 1 obtains；
Fig. 7 is the micro-organization chart for the steel room temperature texture that comparative example 1 of the present invention obtains；
Fig. 8 is the EPMA figures that C element is distributed in the steel room temperature texture that comparative example 1 of the present invention obtains；
Fig. 9 is the EPMA figures of Mn Elemental redistributions in the steel room temperature texture that comparative example 1 of the present invention obtains；
Figure 10 is the SEM figures for the steel room temperature texture that the embodiment of the present invention 2 obtains；
Figure 11 is the SEM figures for the steel room temperature texture that comparative example 2 of the present invention obtains；
Figure 12 is the micro-organization chart for the steel room temperature texture that the embodiment of the present invention 2 obtains；
Figure 13 is the EPMA figures that C element is distributed in the steel room temperature texture that the embodiment of the present invention 2 obtains；
Figure 14 is the EPMA figures of Cu Elemental redistributions in the steel room temperature texture that the embodiment of the present invention 2 obtains；
Figure 15 is the micro-organization chart for the steel room temperature texture that comparative example 2 of the present invention obtains；
Figure 16 is the EPMA figures that C element is distributed in the steel room temperature texture that comparative example 2 of the present invention obtains；
Figure 17 is the EPMA figures of Cu Elemental redistributions in the steel room temperature texture that comparative example 2 of the present invention obtains.
Embodiment
Embodiment 1
The steel billet of consisting of is smelted in ZG-50 vacuum induction melting furnaces, and is forged into the plate that thickness is 75mm
Base；
The C of 0.19wt%；The Si of 1.5wt%；The Mn of 1.3wt%；The P of 0.010wt%；The Al of 0.017wt%；
The S of 0.009wt%；The B of 0.0003wt%；The Fe of surplus；
The slab is heated to 1200 DEG C of insulation 3h in high-temperature box type heating furnace homogenizes alloy element component, so
Hot rolling is carried out to it afterwards, start rolling temperature is 1100 DEG C, through 3 passes to 50mm, is rolled after being cooled to 950 DEG C by 5 passages
Thickness is made and is the thermal simulation experiment hot rolled plate of 15mm, and is lathed Φ 8mm × 12mm cylinder samples；
The sample is heated to 770 DEG C with the speed of 10 DEG C/s, then by sample immediately with 1s-1Rate of deformation compression
10%, keep the temperature 1800s, then water quenching to room temperature.
Comparative example 1
With embodiment 1 difference lies in, after the sample is heated to 770 DEG C with the speed of 10 DEG C/s without deformation,
Directly keep the temperature 1800s, then water quenching to room temperature.
The steel of embodiment 1 and the acquisition of comparative example 1 are observed respectively, as a result referring to Fig. 2, Fig. 3, Fig. 4, Fig. 5, Fig. 6, Fig. 7, figure
8 and Fig. 9, Fig. 2 be the steel that the embodiment of the present invention 1 obtains room temperature texture SEM figures, Fig. 3 is the steel that comparative example 1 of the present invention obtains
The room temperature texture SEM figures of material, Fig. 4 is the micro-organization chart of room temperature texture for the steel that the embodiment of the present invention 1 obtains, and Fig. 5 is this hair
The EPMA figures that C element is distributed in the steel room temperature texture that bright embodiment 1 obtains, Fig. 6 are the steel rooms that the embodiment of the present invention 1 obtains
The EPMA figures of Mn Elemental redistributions, Fig. 7 are the micro-organization charts for the steel room temperature texture that comparative example 1 of the present invention obtains in temperature tissue,
Fig. 8 is the EPMA figures that C element is distributed in the steel room temperature texture that comparative example 1 of the present invention obtains, and Fig. 9 is that comparative example 1 of the present invention obtains
The EPMA figures of Mn Elemental redistributions in the steel room temperature texture obtained.
From Fig. 2 and Fig. 3, obtained after method provided by the invention processing Gang Yangzhong room temperature textures for ferrite and
Martensite (coexistence region austenite) phase.
From Fig. 4~Fig. 8, after method provided by the invention processing, C, Mn martensite and iron in room temperature texture
Significant change occurs for the distribution in ferritic, occurs obvious enrichment in martensite, not deformed to be compared with EPMA pictures that are deforming, sends out
Now under identical soaking time, the experiment steel of deformation C, Mn enrichment of element phenomenon in coexistence region occurs in advance, and is enriched with
Degree improves, and shows that low-carbon silico-manganese steel is deformed in coexistence region and promotes elemental partition.
Embodiment 2
The steel billet of consisting of is smelted in ZG-50 vacuum induction melting furnaces, and is forged into the plate that thickness is 75mm
Base；
The C of 0.18wt%；The Si of 1.58wt%；The Mn of 2.06wt%；The Cu of 0.41wt%；The Ni of 0.33wt%；
The P of 0.008wt%；The S of 0.005wt%；The B of 0.0017wt%；The Fe of surplus；
The slab is heated to 1200 DEG C of insulation 3h in high-temperature box type heating furnace homogenizes alloy element component, so
Hot rolling is carried out to it afterwards, start rolling temperature is 1100 DEG C, through 3 passes to 50mm, is rolled after being cooled to 950 DEG C by 5 passages
Thickness is made and is the thermal simulation experiment hot rolled plate of 15mm, and is lathed Φ 8mm × 12mm cylinder samples；
The sample is heated to 740 DEG C with the speed of 10 DEG C/s, then by sample immediately with 1s-1Rate of deformation compression
10%, keep the temperature 600s, then water quenching to room temperature.
Comparative example 2
With embodiment 2 difference lies in, after the sample is heated to 740 DEG C with the speed of 10 DEG C/s without deformation,
Directly keep the temperature 600s, then water quenching to room temperature.
Observe the steel that embodiment 2 and comparative example 2 obtain respectively, as a result referring to Figure 10, Figure 11, Figure 12, Figure 13, Figure 14,
Figure 15, Figure 16 and Figure 17, Figure 10 are the SEM figures for the steel room temperature texture that the embodiment of the present invention 2 obtains, and Figure 11 is that the present invention compares
The SEM figures for the steel room temperature texture that example 2 obtains, Figure 12 are the microstructures for the steel room temperature texture that the embodiment of the present invention 2 obtains
Figure, Figure 13 are the EPMA figures that C element is distributed in the steel room temperature texture that the embodiment of the present invention 2 obtains, and Figure 14 is implementation of the present invention
The EPMA figures of Cu Elemental redistributions, Figure 15 are the steel room temperature groups that comparative example 2 of the present invention obtains in the steel room temperature texture that example 2 obtains
The micro-organization chart knitted, Figure 16 are that the EPMA that C element is distributed in the steel room temperature texture that comparative example 2 of the present invention obtains schemes, Figure 17
It is the EPMA figures of Cu Elemental redistributions in the steel room temperature texture that comparative example 2 of the present invention obtains.
From Figure 10 and Figure 11, it is ferrite to obtain Gang Yangzhong room temperature textures after method provided by the invention processing
With martensite (coexistence region austenite) phase.
From Figure 12~Figure 17, after method provided by the invention processing, Cu martensite and iron in room temperature texture
Significant change occurs for the distribution in ferritic, occurs obvious enrichment phenomenon in martensite, passes through the not deformed EPMA pictures with deformation
Comparing, find under identical soaking time, the experiment steel of deformation C, Cu enrichment of element phenomenon in coexistence region occurs in advance,
And enrichment degree improves, show that the silico-manganese steel of low-carbon containing Cu promotes alloying element partition in coexistence region deformation energy.
From above-described embodiment, method provided by the invention promotes alloying element in austenite/ferrite dual phase area
Generation partition behavior, not only makes partition behavior carry out in advance, but also improves the enrichment degree in austenite.
The above is only the preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications also should
It is considered as protection scope of the present invention.
Claims (7)
1. a kind of processing method of low-carbon alloy steel, comprises the following steps：
A) low-carbon alloy steel billet is cast, the low-carbon alloy steel billet is forged to slab, the low-carbon alloy steel is low-carbon silicomanganese
Steel；
B) slab is subjected to hot rolling, obtains finish to gauge plate；
C) the finish to gauge plate is warming up to after coexistence region temperature and deformed immediately, water quenching is to room temperature after isothermal holding；The deformation
Deflection is 5%~15%.
2. processing method according to claim 1, it is characterised in that the low-carbon silico-manganese steel includes：The C of 0.18wt%；
The Si of 1.58wt%；The Mn of 2.06wt%；The Cu of 0.41wt%；The Ni of 0.33wt%；The P of 0.008wt%；0.005wt%'s
S；The B of 0.0017wt%；The Fe of surplus；
Or including：The C of 0.19wt%；The Si of 1.5wt%；The Mn of 1.3wt%；The P of 0.010wt%；The Al of 0.017wt%；
The S of 0.009wt%；The B of 0.0003wt%；The Fe of surplus.
3. processing method according to claim 2, it is characterised in that in the step c), coexistence region temperature for 740~
770℃。
4. processing method according to claim 3, it is characterised in that in the step c), with the speed liter of 5~15 DEG C/s
Temperature is to coexistence region temperature.
5. processing method according to claim 1, it is characterised in that in the step c), with 1s-1Rate of deformation become
Shape.
6. processing method according to claim 5, it is characterised in that in the step c), the time of the isothermal holding
For 600~1800s.
7. processing method according to claim 6, it is characterised in that the step b) is specially：
The slab is subjected to hot rolling after 1100~1300 DEG C of 2~4h of isothermal holding, start rolling temperature is 1000~1200 DEG C, warp
3 passes postcoolings obtain finish to gauge plate to 900~1000 DEG C of 5 passes of process after turning.
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