CN107937796A - A kind of method for improving super ferrite stainless steel hot-rolling plate toughness - Google Patents
A kind of method for improving super ferrite stainless steel hot-rolling plate toughness Download PDFInfo
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- CN107937796A CN107937796A CN201711158036.2A CN201711158036A CN107937796A CN 107937796 A CN107937796 A CN 107937796A CN 201711158036 A CN201711158036 A CN 201711158036A CN 107937796 A CN107937796 A CN 107937796A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C21D2211/005—Ferrite
Abstract
The invention belongs to ferritic stainless steel manufacturing field, to solve the problems, such as hot rolled strip cracking phenomena in subsequent coiling process in existing production technology, a kind of method smelting molten steel for improving super ferrite stainless steel hot-rolling plate toughness is provided and is casting continuously to form strand, strand in Hot Rolling Mill tandem rolling into hot rolled plate, continuous furnace isothermal holding is directly entered after the hot rolled unit of hot rolled plate, high pressure water quickly cooling is but batched afterwards.By increasing continuous furnace to hot rolled plate isothermal holding, eliminate and process hardening, significantly the precipitation tendency of containment brittlement phase caused by processing hardening.Hot rolled plate waste heat is made full use of, heating time is short, and energy consumption is low, and manufacture cost is low；Make hot rolled plate through-thickness temperature control uniform, solve the problems, such as to reheat process tabularium surface and the excessive caused thermal stress of center portion temperature difference；Steel plate is reduced in the brittlement phase Precipitation Temperature scope residence time；Hot rolled plate comprehensive mechanical property after processing is good, is not required to be heat-treated hot rolled plate before use.
Description
Technical field
The invention belongs to ferritic stainless steel manufacturing technology field, and in particular to one kind improves super ferrite stainless steel hot
Roll the method for plate toughness.
Background technology
Super ferrite stainless steel is that one kind is rich in chromium (26 ~ 30%) element, contains higher molybdenum（2~4%）The iron of element
Evanohm, its spot corrosion equivalent PREN (Cr%+3.3 × % Mo) is more than 35.Because it is with good corrosion resistance, high heat
The coefficient of conductivity, is the optimal alternative materials of copper alloy and titanium tube mainly for the manufacture of Binhai Generator Station condenser etc..
The addition of Gao Ge, high molybdenum element not only increase the corrosion resistance of ferritic stainless steel, while also bring one
Series of problems.For example Gao Ge, high molybdenum element content can strongly promote the intermetallic compounds such as α ' in steel, σ, χ and Laves
Precipitation.The intermetallic compound such as α ', σ, χ and Laves is brittlement phase, their intercrystalline precipitations can seriously deteriorate material power
Performance is learned, meanwhile, the precipitation of these chromium-rich intermetallic compounds can cause matrix chromium depleted, decline the corrosion resistance of material.
However, in cooling procedure, material will necessarily pass through the humidity province that the intermetallic compound such as α ', σ, χ and Laves easily separates out
Between, how to weaken because the harmful effect that the precipitation of the second phase of brittleness is brought primarily is examined in the stainless steel making processes of super ferrite
The problem of worry, usually annoying metallargist.
The production technology of ferritic stainless steel hot-rolling plate is at present：Smelting molten steel, continuous casting, tandem rolling, high pressure water quickly cool down,
Batch.To solve the above-mentioned problems, in order to avoid the Precipitation Temperature section of the second phase of brittleness, steel band finishing temperature is generally more than
900℃.The cooling procedure inevitable Precipitation Temperature section Jing Guo the second phase of brittleness again is batched after hot rolling, in order to avoid material
Material extended stationary periods in the Precipitation Temperature section of the second phase of brittleness, it is general by the way of quickly cooling down after hot rolling, make steel plate from
900 DEG C drop quickly to less than 400 DEG C, run through brittlement phase Precipitation Temperature section, suppress the precipitation of brittlement phase.
During produced on-site, the finishing temperature of hot rolling is difficult to be accurately controlled more than 900 DEG C, tens degrees Celsius of difference
It is different to have an immense impact on to the performance of steel plate；Subsequent quick cooling procedure can form larger thermal stress in steel plate,
It is difficult to be completely eliminated the deformed microstructure of course of hot rolling generation, remains obvious processing hardening, increases the hand down precipitations of crystal boundary of σ and incline
To dramatically increasing the phenomenon that strip cracks in subsequent coiling process.
Therefore, how to eliminate processing hardening phenomenon, weaken σ and hand down the precipitation tendency of crystal boundary, avoid hot rolled plate coiling process
In cracking, optimized production process, expand product supply scope, be super ferrite stainless steel manufacture during there is an urgent need for solution
A key technique problem certainly.
The content of the invention
In view of the deficiencies of the prior art, the present invention provides one kind to improve super ferrite stainless steel hot-rolling plate toughness
Method, it is therefore an objective to solve the problem of Cracking in super ferrite stainless steel hot-rolling coiling process.
What the present invention was realized by following technical solution：A kind of method for improving super ferrite stainless steel hot-rolling plate toughness,
Smelting molten steel is casting continuously to form strand, and tandem rolling is into hot rolled plate in Hot Rolling Mill for strand, the company of being directly entered after the hot rolled unit of hot rolled plate
Continuous heating furnace carries out isothermal holding, is but batched afterwards using high pressure water quickly cooling.
Comprise the following steps that：（1）Using intermediate frequency vacuum induction furnace smelting molten steel, molten steel is casting continuously to form 200-300mm thickness strands；
（2）For tandem rolling into the hot rolled plate of 2-10mm thickness, it is 980-1150 DEG C to control hot-rolled temperature to strand in Hot Rolling Mill；（3）At insulation
Reason：Continuous furnace is set after Hot Rolling Mill, and hot rolled plate is directly entered continuous furnace and carries out isothermal holding, and holding temperature is
980 DEG C -1150 DEG C, soaking time 10s-300s；（4）Hot rolled plate after isothermal holding is quickly cooled to 400 using high pressure water
Below DEG C, cooling time≤20s, finally batched, obtain super ferrite stainless steel hot-rolling coil.
The optimal holding temperature of the super ferrite stainless steel is 1120 ~ 1150 DEG C, optimal soaking time for 30 ~
50s。
The chemistry of the super ferrite stainless steel into component is by mass percentage：C<0.03%, Si<1%, Mn<1%,
P<0.04, Cr 25.0 ~ 28.0%, Mo 3.0 ~ 4.0%, Ti 0.42 ~ 1.0%, Nb 0.40 ~ 1.0%, N<0.04%, Ni 1.0 ~
3.5%, S<0.04%, surplus is Fe and impurity.
Using this delay heat preservation technology, on the one hand, hot rolled plate completes recrystallization process, and hot rolling band tissue is changed into
Shaft-like recrystal grain, the dislocation density in steel plate strongly reduce, and residual stress is eliminated, while is eliminated in course of hot rolling
The second phase is harmful to caused by dislocation density increase must separate out tendency.On the other hand, the molten operation of rolling of weight in insulating process
Second phase of middle precipitation, directly eliminates the damaging effect of Second Phase Precipitation in steel, thus greatly reduces steel plate and was batching
The tendency to crack in journey.The processing hardening produced using being solved described in this case in current course of hot rolling, greatly reduces at the same time
Harm of brittleness the second phase intercrystalline precipitation to mechanical property of steel plate, avoids cracking of the hot rolled plate in coiling process.
Compared with prior art, the features of the present invention and beneficial effect are：
It is characteristic of the invention that increase continuous furnace after Hot Rolling Mill carries out isothermal holding to hot rolled plate, it is intended to which strip enters
The processing hardening produced in the operation of rolling is eliminated before coiling machine, therefore rationally heating-up temperature is 980 DEG C -1150 DEG C, soaking time
For 10s-300s.The present invention can eliminate processing hardening, significantly containment by increasing continuous furnace to hot rolled plate isothermal holding
The precipitation tendency of the brittlement phase caused by processing hardening.The present invention makes full use of hot rolled plate waste heat, and heating time is short, and energy consumption is low,
It is low to manufacture cost；Make hot rolled plate through-thickness temperature control uniform, in particular for 5-10mm slabs, solve and reheat
Caused by process tabularium surface and center portion temperature difference are excessive the problem of thermal stress；Kept the temperature after hot rolling through annealing furnace, temperature control
Accurately, steel plate is in brittlement phase Precipitation Temperature scope residence time after reducing hot rolling；Hot rolled plate synthesis mechanical property after processing
Can be good, hot rolled plate need not be heat-treated before.
Brief description of the drawings
Fig. 1 is the specific embodiment schematic diagram of the present invention.Fig. 2 is super ferrite stainless steel hot prepared by embodiment 1
Roll plate impact test fracture apperance figure；Fig. 3 is super ferrite stainless steel hot-rolling plate SEM microstructure figures prepared by embodiment 1；
Fig. 4 is the impact test fracture apperance figure of super ferrite stainless steel hot-rolling plate prepared by comparative example；Fig. 5 comparative examples are prepared super
Level ferritic stainless steel hot-rolling plate SEM microstructure figures.
Wherein：1- intermediate frequency vaccum sensitive stoves；2- conticasters；3- roughing mills；4- mm finishing mill units；5- continuous furnaces；6-
High pressure water cooling；7 coiling machines.
Embodiment：
Below in conjunction with attached drawing, the present invention will be further described.The specific embodiment schematic diagram of the present invention is as shown in Figure 1.It is super
The Charpy impact energy of ferritic stainless steel is tested using the mm samples of the mm of 2.5mm × 10 × 55.
Embodiment 1：The chemical composition of super ferrite stainless steel is shown in Table 1.As shown in Figure 1, using intermediate frequency vaccum sensitive stove 1
Smelting molten steel, is casting continuously to form 200mm thickness continuous casting billets through conticaster 2, is rolled after being cooled to 1100 DEG C through roughing mills 3, mm finishing mill unit 4
It is thick to 5.2mm, kept the temperature through continuous furnace 5, holding temperature is 1020 DEG C, controls soaking time 180s, then by high pressure water cooling
But temperature is rapidly cooled to 400 DEG C in 6,15s, is finally batched with coiling machine 7.
Fig. 2 is hot rolling reeling plate room temperature impact fracture apperance figure, and the predominantly dimple in fracture, is allusion quotation as seen from the figure
Type ductile rupture, impact absorbing energy is about 30J after tested.
Fig. 3 is hot rolling reeling plate SEM microstructure figures, and sample crystal grain is in obvious ribbon as seen from the figure, at the same time
There is obvious Second Phase Precipitation thing along crystal boundary.
1 chemical composition of table (wt.%)
| C | Si | Mn | P | S | Cr | Ni | Mo | Cu | Nb | Ti | N |
| 0.025 | 0.400 | 0.230 | 0.022 | 0.020 | 25.570 | 1.980 | 3.680 | 0.050 | 0.370 | 0.140 | 0.016 |
Embodiment 2：The chemical composition of super ferrite stainless steel is shown in Table 2.As shown in Figure 1, smelted using intermediate frequency vaccum sensitive stove 1
Molten steel, 295mm continuous casting billets are casting continuously to form through conticaster 2, and 2mm is rolling to through roughing mills 3, mm finishing mill unit 4 after being cooled to 980 DEG C
Thickness, keeps the temperature through continuous furnace 5, and holding temperature is 1150 DEG C, controls soaking time 40s, then by high pressure water cooling 6, in 10s
Temperature is rapidly cooled to 390 DEG C, is finally batched with coiling machine 7.
The sample Charpy impact energy is 28J after testing, and impact specimen fracture apperance is mainly made of dimple.
2 chemical composition of table (wt.%)
Embodiment 3：The chemical composition of super ferrite stainless steel is shown in Table 3.As shown in Figure 1, smelted using intermediate frequency vaccum sensitive stove 1
Molten steel, 300mm continuous casting billets are casting continuously to form through conticaster 2, and 10mm is rolling to through roughing mills 3, mm finishing mill unit 4 after being cooled to 1150 DEG C
Thickness, keeps the temperature through continuous furnace 5, and holding temperature is 980 DEG C, and control soaking time 300s passes through high pressure water cooling 6 again, in 17s
Temperature is rapidly cooled to 390 DEG C, is finally batched with coiling machine 7.
The sample Charpy impact energy is 28J after testing, and impact specimen fracture apperance is mainly made of dimple, for typical case
Ductile rupture.
3 chemical composition of table (wt.%)
Embodiment 4：The chemical composition of super ferrite stainless steel is shown in Table 3.As shown in Figure 1, smelted using intermediate frequency vaccum sensitive stove 1
Molten steel, 200mm continuous casting billets are casting continuously to form through conticaster 2, and 8mm is rolling to through roughing mills 3, mm finishing mill unit 4 after being cooled to 1150 DEG C
Thickness, keeps the temperature through continuous furnace 5, and holding temperature is 1135 DEG C, and control soaking time 50s passes through high pressure water cooling 6 again, in 17s
Temperature is rapidly cooled to 390 DEG C, is finally batched with coiling machine 7.
The sample Charpy impact energy is 32J after testing, and impact specimen fracture apperance is mainly made of dimple, for typical case
Ductile rupture.
Embodiment 5：The chemical composition of super ferrite stainless steel is shown in Table 2.As shown in Figure 1, using intermediate frequency vaccum sensitive stove 1
Smelting molten steel, 295mm continuous casting billets are casting continuously to form through conticaster 2, are rolling to after being cooled to 1100 DEG C through roughing mills 3, mm finishing mill unit 4
5mm is thick, is kept the temperature through continuous furnace 5, and holding temperature is 1140 DEG C, controls soaking time 30s, then by high pressure water cooling 6,
Temperature is rapidly cooled to 390 DEG C in 10s, is finally batched with coiling machine 7.
The sample Charpy impact energy is 32J after testing, and impact specimen fracture apperance is mainly made of dimple, for typical case
Ductile rupture.
Embodiment 6：The chemical composition of super ferrite stainless steel is shown in Table 1.As shown in Figure 1, using intermediate frequency vaccum sensitive stove 1
Smelting molten steel, is casting continuously to form 200mm thickness continuous casting billets through conticaster 2, is rolled after being cooled to 1100 DEG C through roughing mills 3, mm finishing mill unit 4
It is thick to 10mm, kept the temperature through continuous furnace 5, holding temperature is 1130 DEG C, controls soaking time 40s, then by high pressure water cooling
Temperature is rapidly cooled to 400 DEG C in 6,15s, is finally batched with coiling machine 7.
The sample Charpy impact energy is 31J after testing, and impact specimen fracture apperance is mainly made of dimple, for typical case
Ductile rupture.
Comparative example：The chemical composition of super ferrite stainless steel is shown in Table 1.Using 1 smelting molten steel of intermediate frequency vaccum sensitive stove, warp
Conticaster 2 is rolling to 4.9mm thickness into 200mm continuous casting billets after being cooled to 1100 DEG C through roughing mills 3, mm finishing mill unit 4, water cooled
Temperature is cooled to 400 DEG C afterwards, is finally batched with coiling machine 7.
Fig. 4 is comparative example hot rolling reeling plate room temperature impact fracture apperance figure, is mainly cleavage fracture, through surveying as seen from the figure
It is about 18J to try Charpy impact energy, and impact flexibility is poor.
Fig. 5 is comparative example hot rolling reeling plate SEM microstructure figures, and sample crystal grain is in obvious isometric as seen from the figure
Shape, while significantly reduced along the white Second Phase Precipitation thing of crystal boundary.
As can be seen from the above results, using the hot-rolled coil of the method for the invention acquisition, its toughness improves about 2 times,
The harmful second precipitation for handing down crystal boundary can be substantially reduced at the same time.Efficiently solve the skill of cracking of the hot rolled plate in coiling process
Art problem.
Claims (4)
- A kind of 1. method for improving super ferrite stainless steel hot-rolling plate toughness, it is characterised in that：Smelting molten steel is casting continuously to form strand, Strand tandem rolling in Hot Rolling Mill is directly entered continuous furnace into hot rolled plate, after the hot rolled unit of hot rolled plate and carries out at insulation Reason, is but batched afterwards using high pressure water quickly cooling.
- A kind of 2. method for improving super ferrite stainless steel hot-rolling plate toughness according to claim 1, it is characterised in that： Comprise the following steps that：（1）Using intermediate frequency vacuum induction furnace smelting molten steel, molten steel is casting continuously to form 200-300mm thickness strands；（2）Strand For tandem rolling into the hot rolled plate of 2-10mm thickness, it is 980-1150 DEG C to control hot-rolled temperature in Hot Rolling Mill；（3）Isothermal holding：Hot rolling Continuous furnace is set after unit, hot rolled plate is directly entered continuous furnace and carries out isothermal holding, holding temperature for 980 DEG C- 1150 DEG C, soaking time 10s-300s；（4）Hot rolled plate after isothermal holding is quickly cooled to less than 400 DEG C using high pressure water, Cooling time≤20s, finally batched, obtain super ferrite stainless steel hot-rolling coil.
- A kind of 3. method for improving super ferrite stainless steel hot-rolling plate toughness according to claim 2, it is characterised in that： The holding temperature is 1120 ~ 1150 DEG C, and soaking time is 30 ~ 50s.
- 4. the method that any one according to claims 1 to 3 improves super ferrite stainless steel hot-rolling plate toughness, it is special Sign is：The chemistry of the super ferrite stainless steel into component is by mass percentage：C<0.03%, Si<1%, Mn<1%, P <0.04, Cr 25.0 ~ 28.0%, Mo 3.0 ~ 4.0%, Ti 0.42 ~ 1.0%, Nb 0.40 ~ 1.0%, N<0.04%, Ni 1.0 ~ 3.5%, S<0.04%, surplus is Fe and impurity.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114086087A (en) * | 2021-11-29 | 2022-02-25 | 中北大学 | Method for treating embrittled high-chromium ferritic stainless steel plate |
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| CN114086087B (en) * | 2021-11-29 | 2022-07-26 | 中北大学 | Method for treating embrittled high-chromium ferritic stainless steel plate |
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| Publication number | Publication date |
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| CN107937796B (en) | 2020-07-07 |
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