CN108348990A - Austenitic stainless steel and its manufacturing method with excellent resistance to tangerine peel - Google Patents
Austenitic stainless steel and its manufacturing method with excellent resistance to tangerine peel Download PDFInfo
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- CN108348990A CN108348990A CN201680065899.2A CN201680065899A CN108348990A CN 108348990 A CN108348990 A CN 108348990A CN 201680065899 A CN201680065899 A CN 201680065899A CN 108348990 A CN108348990 A CN 108348990A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/002—Stainless steels
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0637—Accessories therefor
- B22D11/068—Accessories therefor for cooling the cast product during its passage through the mould surfaces
- B22D11/0682—Accessories therefor for cooling the cast product during its passage through the mould surfaces by cooling the casting wheel
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
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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
- C21D8/0236—Cold rolling
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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
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
Disclose austenitic stainless steel and its manufacturing method with excellent resistance to tangerine peel.In the austenitic stainless steel with excellent resistance to tangerine peel, embodiment according to the present invention, including the ratio between average grain size (Gs) and the average grain size (Gi) comprising internal grain in the second area of surface microstructure in the first region Gs/Gi are 0.5 or smaller, the first area corresponds to 10% or smaller depth of the overall thickness apart from the surface of austenitic stainless steel of austenitic stainless steel, which corresponds to 10% or deeper depth of the overall thickness apart from the surface of austenitic stainless steel than austenitic stainless steel.Therefore, the surface roughness deterioration caused by the tangerine peel in steel surface is even also possible to prevent after being post-processed to stainless steel, increase crystallite dimension to reduce the intensity of austenitic stainless steel simultaneously, and cost can also be reduced by replacing copper pipe as air-conditioning refrigerant pipe or aluminum pipe with stainless steel tube.
Description
Technical field
This disclosure relates to the austenitic stainless steels with excellent resistance to tangerine peel (orange peel resistance)
And its manufacturing method, and even exist more particularly, to the average grain size at the different depth by controlling stainless steel
Also it can prevent the surface roughness caused by the tangerine peel of steel surface from deteriorating after being post-processed to stainless steel, increase simultaneously
The size of crystal grain is to drop the low intensive austenitic stainless steel with excellent resistance to tangerine peel and manufacture the austenitic stainless steel
Method.
Background technology
Attempt the refrigerant pipe that stainless steel is applied to domestic air conditioning and air conditioning for automobiles because stainless steel have it is excellent resistance to
Corrosivity and cheap price.
However, the refrigerant pipe due to air-conditioning is limited by installation space, so in many cases, construction pipe is substantially
Make the work that pipe is bent along with manpower.Usually used copper pipe or aluminum pipe is sufficiently soft without will produce any ask due to them
It inscribes, but general stainless steel has not having the required flexibility of construction pipe.
Metal material is being subjected to deforming, such as meeting processing hardening when stretching or compression, and when they are subjected to higher change
When shape, become firmer.It is the comprehensive function for stretching and compressing to make pipe bending, and as bending degree is bigger, and material will become
It obtains harder.Particularly, when 304 steel for being most widely used as austenitic stainless steel are used for air-conditioner pipe, since work-hardening capacity is high,
So making pipe bending be very difficult with manpower in the space of installing pipe.
In order to overcome the problem, using the method for reducing stainless hardness of steel by increasing crystallite dimension (that is, grain size).No
The intensity of rust steel is reduced with the increase of crystallite dimension.However, with the increase of crystallite dimension, it is in the rear surface of processing
The tangerine peel of uneven defect.Therefore, the intensity of stainless steel is only difficult to decrease by increasing crystallite dimension.Tangerine peel should be removed,
Because it compromises beauty, and removes tangerine peel by polishing and need additional cost and time.
(patent document 0001) South Korea speciallys permit Patent Application Publication the 10-2010-0020446th
Invention content
Technical problem
The embodiment of present disclosure is intended to provide the austenitic stainless steel with excellent resistance to tangerine peel, passes through control
Average grain size at the different depth of stainless steel even can also be prevented due to steel after being post-processed to stainless steel
Surface roughness deterioration caused by the tangerine peel on surface, while increasing the size of crystal grain to reduce intensity.
In addition, the embodiment of present disclosure is intended to provide austenitic stainless steel of the manufacture with excellent resistance to tangerine peel
Method, the austenitic stainless steel can prevent the surface roughness caused by tangerine peel from deteriorating, and wherein austenitic stainless steel is logical
It crosses control delta ferrite phase content and the band of the growth of surface microstructure is thus inhibited to cast to cast.
Technical solution
According to present disclosure embodiment, in the austenitic stainless steel with excellent resistance to tangerine peel, including
The average grain size Gs of surface microstructure in the first region and the average crystal grain for including internal grain in the second area
The ratio between size Gi Gs/Gi can be 0.5 or smaller, and the first area is corresponding to austenitic stainless steel apart from austenitic stainless steel
10% or smaller depth of the overall thickness on surface, the second area correspond to than austenitic stainless steel apart from austenite not
10% deeper depth of the overall thickness for steel surface of becoming rusty.
An embodiment according to the present invention, austenitic stainless steel can include 0.1 weight % to 0.65 weight % (weights
Measure percentage) silicon (Si), the manganese (Mn) of 1.0 weight % to 3.0 weight %, 6.5 weight % to 10.0 weight % nickel (Ni),
Copper (Cu), the 0.13 weight % of the chromium (Cr) of 16.5 weight % to 18.5 weight %, 6.0 weight % or less (other than zero)
Or the carbon (C) and nitrogen (N) and iron (Fe) and other inevitable impurity of less (other than zero).
The average grain size Gs of an embodiment according to the present invention, surface microstructure can be 100 μm or smaller.
An embodiment according to the present invention, austenitic stainless steel can be manufactured by band casting.
An embodiment according to the present invention, when austenitic stainless steel when casting, is retained by band casting after solidification
Delta ferrite phase content can be 5 weight % or more.
The delta ferrite phase content of an embodiment according to the present invention, the cold rolling microstructure of austenitic stainless steel can be 0.5
Weight % or more.
According to present disclosure embodiment, by by stainless steel across a pair of of rotating roller so that described
Stainless steel is frozen into method of the band casting of solid to manufacture the austenitic stainless steel with excellent resistance to tangerine peel, the method packet
It includes：Cast austenitic stainless and the element that austenitic stainless steel is controlled according to formula (1) make the δ iron elements that solidification retains later
The content Δ of body phase is 5 weight % or more, to manufacture hot rolled steel plate：
Δ=((Cr+Mo+1.5Mn+0.5Nb+2Ti+18)/(Ni+0.3Cu+30* (C+N)+0.5Mn+36)+0.262) ×
161-161, formula (1)
Herein, the symbol of element of formula (1) indicates the weight percent (weight %) of respective element.
An embodiment according to the present invention, austenitic stainless steel can include 0.1 weight % to 0.65 weight % (weights
Measure percentage) silicon (Si), the manganese (Mn) of 1.0 weight % to 3.0 weight %, 6.5 weight % to 10.0 weight % nickel (Ni),
Copper (Cu), the 0.13 weight % of the chromium (Cr) of 16.5 weight % to 18.5 weight %, 6.0 weight % or less (other than zero)
Or the carbon (C) and nitrogen (N) and iron (Fe) and other inevitable impurity of less (other than zero).
An embodiment according to the present invention, the method further include：Hot rolled steel plate is heat-treated, then with
50% or higher total reduction (reduction rate) carries out cold rolling to hot rolled steel plate, thus manufactures cold-rolled steel sheet, wherein
The delta ferrite phase content of the cold rolling microstructure of cold-rolled steel sheet is 0.5 weight % or more.
Advantageous effect
The embodiment of present disclosure is even also possible to prevent after the post-processing of austenitic stainless steel due to Ovshinsky
Surface roughness deterioration caused by the tangerine peel of body stainless steel surface, while increasing crystallite dimension to reduce the strong of austenitic stainless steel
Degree, and cost can be reduced by replacing copper pipe as air-conditioning refrigerant pipe or aluminum pipe with stainless steel tube.
In addition, thus the embodiment of present disclosure can be by delta ferrite phase content and inhibiting surface via control
The band casting of the growth of crystal grain carrys out cast austenitic stainless and the surface roughness caused by tangerine peel is prevented to deteriorate.
Description of the drawings
Fig. 1 is to describe to be carried according to the band casting for manufacturing austenitic stainless steel of an embodiment of present disclosure
The schematic diagram of the equipment of confession.
Fig. 2 is that the section of the austenitic stainless steel cold-rolled plate for describing an embodiment according to present disclosure regards
Figure.
Fig. 3 is the photograph of the Austenitic stainless steel pipe for the embodiment according to present disclosure for showing 90 degree of bending
Piece.
Fig. 4 is the photo on the surface for the Austenitic stainless steel pipe for showing Fig. 1.
Fig. 5 is the photo on the surface for showing typical Austenitic stainless steel pipe.
Fig. 6 is the photo of the section microscopic structure for the Austenitic stainless steel pipe for showing Fig. 1.
Fig. 7 is the photo for the section microscopic structure for showing typical Austenitic stainless steel pipe.
Fig. 8 is crystallite dimension and Austria of the austenitic stainless steel for describing an embodiment according to present disclosure
The figure of surface roughness when family name's body stainless steel tube bends to 90 degree.
Specific implementation mode
According to present disclosure embodiment, in the austenitic stainless steel with excellent resistance to tangerine peel, including
The average grain size Gs of surface microstructure in the first region and the average crystal grain for including internal grain in the second area
The ratio between size Gi Gs/Gi can be 0.5 or smaller, and the first area is corresponding to austenitic stainless steel apart from austenitic stainless steel
10% or smaller depth of the overall thickness on surface, the second area correspond to than austenitic stainless steel apart from austenite not
10% deeper depth of the overall thickness for steel surface of becoming rusty.
Invention embodiment
Hereinafter, the embodiment for describing present disclosure in detail with reference to the accompanying drawings.There is provided following embodiments with
The technological concept of present disclosure is pass on to those skilled in the art.However, present disclosure is not limited to these realities
Scheme is applied, but can be implemented in another form.In the accompanying drawings, in order to present disclosure it is clear for the sake of, can not show
The part unrelated with specification, and for easy understanding, the size of component is shown with being more or less amplified.
According to present disclosure embodiment, the austenitic stainless steel with excellent resistance to tangerine peel can include
The silicon (Si) of 0.1 weight % to 0.65 weight % (weight percent), manganese (Mn), 6.5 weights of 1.0 weight % to 3.0 weight %
Measure the nickel (Ni) of % to 10.0 weight %, the chromium (Cr) of 16.5 weight % to 18.5 weight %, 6.0 weight % or less (in addition to
Except zero) copper (Cu), 0.13 weight % or less (other than zero) carbon (C) and nitrogen (N) and iron (Fe) and other not
Evitable impurity.
Hereinafter, description is constituted to the number of the element of the austenitic stainless steel with excellent flexibility according to present disclosure
The reasons why value limitation.
Silicon (Si) can be added in the range of 0.1 weight % to 0.65 weight %.
Since silicon (Si) is the element that must be added for deoxidation, it is possible to add the silicon of 0.1 weight % or more
(Si)。
However, if silicon (Si) too high levels, material may harden, and be combined to form field trash with oxygen, cause resistance to
Corrosive deterioration.Therefore, maximum silicon (Si) content can be limited to 0.65 weight %.
Manganese (Mn) can be added in the range of 1.0 weight % to 3.0 weight %.
Since manganese (Mn) is the element that must be added for the stabilization of deoxidation and raising austenite phase, can add
The manganese (Mn) of 1.0 weight % or more keeps austenite to balance.However, if manganese (Mn) too high levels, material it is corrosion-resistant
Property may be deteriorated, therefore can maximum manganese (Mn) content be limited to 3.0 weight %.
Nickel (Ni) can be added in the range of 6.5 weight % to 10.0 weight %.
If nickel (Ni) and chromium (Cr) add together, corrosion resistance, such as pitting corrosion resistance can be improved, and in addition such as
Fruit increases nickel (Ni) content, then austenitic steel may be softened.
Further, since nickel (Ni) contributes to improve the mutually stable element of austenitic stainless steel, therefore 6.5 can be added
The nickel (Ni) of weight % or more keeps austenite to balance.However, if nickel (Ni) too high levels, austenitic stainless steel
Manufacturing cost can increase, and therefore, can maximum nickel (Ni) content be limited to 10.0 weight %.
Chromium (Cr) can be added in the range of 16.5 weight % to 18.5 weight %.
Since chromium (Cr) is the element that must be added to improve corrosion resistance, addition 16.5 may be generally needed
The chromium (Cr) of weight % or more.However, if chromium (Cr) too high levels, austenite phase can be hardened, and be manufactured into
This can increase.Therefore, maximum chromium (Cr) content can be limited to 18.5 weight %.
Copper (Cu) can be added in 6.0 weight % or less range.
Copper (Cu) can soften austenitic stainless steel.However, if copper (Cu) too high levels, hot workability may quilt
Deterioration, and austenite phase may be hardened.Therefore, copper max (Cu) content can be limited to 6.0 weight %.
Carbon (C)+nitrogen (N) can be with 0.13 weight % or less additions.
Carbon (C) and nitrogen (N) (it is interstitial solid solution hardening element) can harden austenitic stainless steel, if carbon (C) and
Nitrogen (N) content is high, then the deformation martensite generated during processing can be hardened to increase the workhardness of material.Cause
This, it may be necessary to carbon (C) and nitrogen (N) content are limited, and in this disclosure, carbon (C)+nitrogen (N) content can be limited
In 0.13 weight % or less.
According to present disclosure embodiment, in the austenitic stainless steel with excellent resistance to tangerine peel, including
The average grain size Gs of surface microstructure in the first region and the average crystal grain for including internal grain in the second area
The ratio between size Gi Gs/Gi can be 0.5 or smaller, and the first area is corresponding to austenitic stainless steel apart from austenitic stainless steel
10% or smaller depth of the overall thickness on surface, the second area correspond to than austenitic stainless steel apart from austenite not
10% deeper depth of the overall thickness for steel surface of becoming rusty.
That is, by keeping being distributed in the size of the surface microstructure in the first area of neighbouring austenite stainless steel surface to be less than
The size of the internal grain of austenitic stainless steel, when the pipe made of austenitic stainless steel can prevent it to be bent on the surface
Generate tangerine peel.
For example, the average grain size Gs of surface microstructure can be 100 μm or smaller.Meanwhile the average crystal grain of internal grain
Size Gi can be more than 100 μm.
According to present disclosure embodiment, the austenitic stainless steel with excellent resistance to tangerine peel can pass through by
Stainless steel is across a pair of of rotating roller so that it is frozen into the band casting of solid to manufacture.
Fig. 1 is to describe the band casting for manufacturing austenitic stainless steel of an embodiment according to present disclosure
The schematic diagram of the equipment provided.
It is the steel casting method that hot rolled thin strip is directly produced by molten steel with casting.Band casting can be by omitting course of hot rolling innovation
Property reduce manufacturing cost, equipment investment cost, energy expenditure and polluted gas discharge etc..
In fig. 1 it is shown that for the double roller tape casting machine with casting.Referring to Fig.1, molten steel can be put into ladle 2,
Molten steel can enter turntable 3 along the mouth of a river.Into turntable 3 molten steel can be supplied to by the melt injection mouth of a river 4 mounted on
Between the edge dams 6 at 1 both ends of casting roll between casting roll 1, then solidify.In molten metal region between casting roll 1,
The surface of molten metal can be protected by preventing the falcate shield (meniscus shield) 5 of oxidation, and can be injected
Gas appropriate is suitably to adjust atmosphere.When molten steel is escaped from the roll gap that casting roll 1 merges, thin plate 7 can be produced simultaneously
Make its stretching.Then, thin plate 7 can be rolled across roller mill 8, then be cooled down and wound in winding apparatus 9.
It can carry out with casting so that liquid molten steel is directly cast as the plate that thickness is 1mm to 5mm, then apply to the plate high
Cooling velocity.That is, may be used in double roller tape casting machine manufacture hot rolling (hot coil) with casting.Double roller tape casting machine can be with
Molten steel is supplied between the casting roll 1 rotated in mutually opposite directions and between the edge dams 6 mounted on 1 side of casting roll, and
Surface by being water-cooled casting roll distributes a large amount of heat, thus cast steel.At this point, due to high cooling velocity, Ke Yi
The shell of solidification is formed on the surface of casting roll, and after the casting, can continue on-line rolling to manufacture thickness as 1mm
To the thin hot rolled steel plate of 5mm.Due to band casting can direct casted thin plate, so can be omitted through continuous casting and hot rolling technology with casting
Manufacture the process of slab.
Particularly, when manufacturing austenitic stainless steel by general continuous casting, delta ferrite phase can be generated in initial solidification
To ensure the stability of solidification, the solidification of austenite phase then can be carried out.According to the type of steel, in the δ retained during casting
The content of ferritic phase can be in the range of about 1 weight % to about 10 weight %.That is, when casting general slab, delta ferrite
It can mutually be retained in slab.
However, slab can heat 2 hours or longer to carry out hot rolling in reheating furnace.At this point, most of delta ferrite
It can mutually be changed by solid phase and be decomposed into austenite phase, then can carry out hot rolling at high temperature so that in slab casting tissue
Existing major part delta ferrite can mutually be decomposed.Therefore, the delta ferrite of general hot rolling made of austenitic stainless steel contains
Amount can be 0.5 weight % or less.
Since band casting uses water chill rolls by the direct casted thin plate of molten steel, it is convenient to omit reheat process and the hot rolling of slab
Process, therefore the high delta ferrite phase content that 5 weight % can be obtained or more.In addition, most of delta ferrites may mutually retain
On the surface of stainless steel plate so that the delta ferrite retained in stainless steel surface can mutually inhibit the growth of crystal grain.
Therefore, the delta ferrite phase by that will be retained in the tissue according to the austenitic stainless steel hot-rolled steel with casting manufacture
Content control be 5 weight % or more, the content of delta ferrite phase in the tissue retained in final products can be increased.Therefore,
The surface microstructure being distributed in the region on the surface of neighbouring austenitic stainless steel can be formed as the inside than austenitic stainless steel
The smaller size of crystal grain.
That is, being retained in the delta ferrite in the austenitic stainless steel hot-rolled steel according to an embodiment of present disclosure
The content of phase can be 5 weight % or more.
Content Δ control in order to be retained in the delta ferrite phase in cast austenitic stainless steel after solidifying is 5
Weight % or more, can be according to following formula (1) control element：
Δ=((Cr+Mo+1.5Mn+0.5Nb+2Ti+18)/(Ni+0.3Cu+30* (C+N)+0.5Mn+36)+0.262) ×
161-161, formula (1)
Herein, the symbol of element of formula (1) indicates the weight percent (weight %) of respective element.
Later, hot rolled steel plate can be heat-treated, cold rolling is then carried out with 50% or higher total reduction, thus
Manufacture austenitic stainless steel cold-rolled steel sheet.
According to present disclosure embodiment, pass through the austenitic stainless steel cold-rolled plate of above-mentioned cold-rolling process cold rolling
The delta ferrite phase content of cold rolling microstructure can be 0.5 weight % or less.
Hereinafter, present disclosure will be more fully described by embodiment.
As shown in table 1, by that will be 5 by the content Δ control of the delta ferrite phase of the hot rolled steel plate cast with casting
Weight % or more manufactures austenitic stainless steel according to present disclosure.Then, it is carried out with 50% or higher total reduction cold
It rolls to manufacture cold-rolled steel sheet, and cold-rolled steel sheet is made to extend 15%.Later, the surface roughness (tangerine peel) of gained steel plate is measured.
For stretching, manufacturer's standard drawing sheet, such as JIS 13B, or plank can be stretched as former state.15% in the same terms
Under be compared, and the feature of present disclosure not necessarily only obtains after 15% extension.
Measure be included in corresponding to austenitic stainless steel the overall thickness apart from austenite stainless steel surface 10% or more
The average grain size Gs of surface microstructure in the region of small depth and included in corresponding to the distance than austenitic stainless steel
The average grain size Gi of internal grain in the region of 10% deeper depth of the overall thickness of austenite stainless steel surface, and
And the ratio between average grain size Gs and average grain size Gi Gs/Gi is presented.
The average grain size Gs of surface microstructure refers to being included in corresponding to austenitic stainless steel apart from austenite stainless
The average grain size of crystal grain in the region of 10% or smaller depth of the overall thickness of steel surface.In addition, internal grain
Average grain size Gi refers to being included in the overall thickness apart from austenite stainless steel surface corresponded to than austenitic stainless steel
The average grain size of crystal grain in the region of 10% deeper depth.
[table 1]
| Δ | Method | Gs/Gi | Presence or absence of tangerine peel | |
| Embodiment 1 | 5.1 | Band casting | 0.47 | ○ |
| Embodiment 2 | 6.2 | Band casting | 0.42 | ○ |
| Embodiment 3 | 7.2 | Band casting | 0.37 | ○ |
| Embodiment 4 | 8.5 | Band casting | 0.42 | ○ |
| Comparative example 1 | 5.5 | Continuous casting | 1.03 | × |
| Comparative example 2 | 6.4 | Continuous casting | 0.95 | × |
| Comparative example 3 | 4.1 | Band casting | 0.74 | × |
| Comparative example 4 | 6.2 | Continuous casting | 0.97 | × |
With reference to table 1, when by being 5 weight % with casting manufacture austenitic stainless steel and by the control of the content of delta ferrite phase
Or more when, in the final product without generate tangerine peel.In addition, when being 5 weight % by the content control of delta ferrite phase, table
The ratio between the average grain size Gs of face crystal grain and the average grain size Gi of internal grain Gs/Gi are 0.5 or smaller.
Table 2 shows the measured surface grain size of embodiment 1 to 4 and comparative example 1 to 4.
[table 2]
| Surface grain size (Gs, μm) | Tangerine peel | |
| Embodiment 1 | 14 | ○ |
| Embodiment 2 | 40 | ○ |
| Embodiment 3 | 58 | ○ |
| Embodiment 4 | 85 | ○ |
| Comparative example 1 | 105 | × |
| Comparative example 2 | 145 | × |
| Comparative example 3 | 192 | × |
| Comparative example 4 | 280 | × |
With reference to table 2, there is excellent tangerine peel in surface grain size Gs is 100 μm or smaller stainless steel plate, and
Obviously there is tangerine peel, such as comparative example in the stainless steel plate more than 100 μm in surface grain size Gs.
Measure the surface grain size and internal grain size of embodiment 1 to 4 and comparative example 1 to 4, and surface microstructure
The ratio between size and internal grain size are shown in Table 3.
[table 3]
| Surface grain size (Gs, μm) | Internal grain size (Gi, μm) | Gs/Gi | Presence or absence of tangerine peel | |
| Embodiment 1 | 14 | 30 | 0.47 | ○ |
| Embodiment 2 | 40 | 95 | 0.42 | ○ |
| Embodiment 3 | 58 | 155 | 0.37 | ○ |
| Embodiment 4 | 85 | 201 | 0.42 | ○ |
| Comparative example 1 | 105 | 102 | 1.03 | × |
| Comparative example 2 | 145 | 153 | 0.95 | × |
| Comparative example 3 | 192 | 260 | 0.74 | × |
| Comparative example 4 | 280 | 290 | 0.97 | × |
As shown in table 3, it is 100 μm or smaller and surface grain size Gs and internal grain ruler in surface grain size Gs
Under the conditions of the ratio between very little Gi Gs/Gi are 0.5 or smaller, there is excellent resistance to tangerine peel.
In table 4, by that will be 5 weight % by the content Δ control of the delta ferrite phase of the hot rolled steel plate cast with casting
Or more, manufacture austenitic stainless steel.
Then, cold rolling is carried out with 50% total reduction to manufacture Austenitic stainless steel pipe.It will be difficult to understand using hand bender
Family name's body stainless steel tube is bent 90 degree, then measures the surface roughness (tangerine peel) of bending part.Hand bender has for applying
There is the deformation of non-uniform curvature radius, and hand bender can be replaced using another equipment.In addition, in order to apply uniformly
Deformation, using 90 degree of angle, although the feature of present disclosure can also be obtained using another angle.
Fig. 2 is that the section of the austenitic stainless steel cold-rolled plate for describing an embodiment according to present disclosure regards
Figure.Fig. 3 is the photo of the Austenitic stainless steel pipe for the embodiment according to present disclosure for showing 90 degree of bending.
It measures and is included in the overall thickness apart from 100 surface of austenitic stainless steel for corresponding to austenitic stainless steel 100
The average grain size Gs of surface microstructure in the first area A1 of 10% or smaller depth and included in correspond to than Ovshinsky
In the second area A2 of 10% deeper depth of the overall thickness apart from 100 surface of austenitic stainless steel of body stainless steel 100
The average grain size Gi of internal grain, and the ratio between average grain size Gs and average grain size Gi Gs/Gi is presented.
[table 4]
| Surface grain size (Gs, μm) | Presence or absence of tangerine peel | |
| Embodiment 1 | 35 | ○ |
| Embodiment 2 | 50 | ○ |
| Embodiment 3 | 69 | ○ |
| Embodiment 4 | 95 | ○ |
| Comparative example 1 | 110 | × |
| Comparative example 2 | 150 | × |
| Comparative example 3 | 170 | × |
| Comparative example 4 | 250 | × |
As shown in the embodiment of table 4, in surface grain size is 100 μm or smaller pipe, there is excellent tangerine
Skin, and as shown in the comparative example of table 4, in pipe of the surface grain size more than 100 μm, hence it is evident that tangerine peel occur.
That is, there is tangerine peel in pipe of the surface grain size more than 100 μm.Therefore, by protecting surface grain size Gs
The crystallite dimension of stainless steel can be passed through in 100 μm or smaller and the size Gi for increasing internal grain, the intensity of stainless steel by holding
Increase reduce.
For example, the average grain size Gi of the internal grain of austenitic stainless steel can be more than 100 μm.
[table 5]
| Surface grain size (Gs, μm) | Internal grain size (Gi, μm) | Gs/Gi | Presence or absence of tangerine peel | |
| Embodiment 1 | 35 | 101 | 0.35 | ○ |
| Embodiment 2 | 50 | 152 | 0.33 | ○ |
| Embodiment 3 | 69 | 169 | 0.41 | ○ |
| Embodiment 4 | 95 | 210 | 0.45 | ○ |
| Comparative example 1 | 110 | 102 | 1.08 | × |
| Comparative example 2 | 150 | 153 | 0.98 | × |
| Comparative example 3 | 170 | 260 | 0.65 | × |
| Comparative example 4 | 250 | 201 | 1.24 | × |
As table 5 embodiment in, if surface grain size Gs be 100 μm or smaller and surface grain size Gs with
The ratio between internal grain size Gi Gs/Gi are 0.5 or smaller, then excellent resistance to tangerine peel occur.
Fig. 4 is the photo on the surface for the Austenitic stainless steel pipe for showing Fig. 1.Fig. 5 is to show typical Austenitic stainless steel pipe
Surface photo.Fig. 6 is the photo of the section microscopic structure for the Austenitic stainless steel pipe for showing Fig. 1.Fig. 7 is to show typical Austria
The photo of the section microscopic structure of family name's body stainless steel tube.
More specifically, Fig. 4 and 6 is shown according to micro- group of the surface of the Austenitic stainless steel pipe of embodiment 3 and section
It knits and Fig. 5 and 7 shows surface and section microscopic structure according to the Austenitic stainless steel pipe of comparative example 3.
With reference to table 4, table 5 and Fig. 5 to 7, it can be seen that according to the austenite of an embodiment of present disclosure not
Not occurring tangerine peel on the surface of rust steel pipe, the size of the crystal grain on adjacent stainless steel surface is less than the size of other crystal grain, because
In the microscopic structure of section, the average-size of the crystal grain in the region on the surface of adjacent stainless steel is 100 μm or smaller, and stainless
The average-size of crystal grain inside steel is more than 100 μm.Therefore, the size of the crystal grain in the region on adjacent stainless steel surface is less than other
The size of the crystal grain in region.In addition, in the surface according to the Austenitic stainless steel pipe of comparative example, tangerine peel, therefore appearance are generated
It is deteriorated, and in the microscopic structure of section, the crystal grain in the region on adjacent stainless steel surface is dimensioned slightly smaller than the interior of stainless steel
The size of portion's crystal grain, the wherein average-size of the crystal grain in the region on adjacent stainless steel surface are more than 100 μm.
Fig. 8 is crystallite dimension and Austria of the austenitic stainless steel for describing an embodiment according to present disclosure
The figure of surface roughness when family name's body stainless steel tube bends to 90 degree.
With reference to Fig. 8, it can be seen that by the size Gs of limiting surface crystal grain, manufacture can inhibit tangerine peel while increase stainless
The average grain size of steel is to reduce the stainless steel tube of the intensity of stainless steel.That is, as seen from Figure 8, in a comparative example, surface
Roughness Rz is more than 10 μm and to generate tangerine peel, and in embodiments, surface roughness Rz is that 10 μm or smaller to inhibit
Tangerine peel, although the size Gi of internal grain increases as comparative example.
More specifically, as shown in Figure 8, the embodiment pair that the wherein average grain size Gi of internal grain is 100 μm
Ying Yu wherein surface roughness Rz are about 4.5 μm so that not generating the austenitic stainless steel of tangerine peel manufactured according to embodiment 1
Pipe, the embodiment that the average grain size Gi of wherein internal grain is 150 μm are about 4.8 corresponding to wherein surface roughness Rz
μm so that do not generate the Austenitic stainless steel pipe manufactured according to embodiment 2 of tangerine peel, and wherein internal grain average crystalline substance
The embodiment that particle size Gi is 200 μm is about 5.2 μm so that not generating the basis of tangerine peel corresponding to wherein surface roughness Rz
The Austenitic stainless steel pipe that embodiment 4 manufactures.
Unlike this, it is thick that the comparative example that the wherein average grain size Gi of internal grain is 100 μm corresponds to wherein surface
Rugosity Rz is about 12 μm of Austenitic stainless steel pipes manufactured according to comparative example 1 for generate tangerine peel, and wherein internal grain is flat
The comparative example that equal crystallite dimension Gi is 150 μm correspond to wherein surface roughness Rz be about 19 μm so that generate tangerine peel according to than
Compared with the Austenitic stainless steel pipe that example 2 manufactures, and the average grain size Gi of wherein internal grain is 200 μm of embodiment pair
Ying Yu wherein surface roughness Rz are about 22 μm so that generating the Austenitic stainless steel pipe of tangerine peel manufactured according to comparative example 4.
Although present disclosure has been described in detail with reference to exemplary implementation scheme, those skilled in the art should
Understand, without departing from the spirit and scope in the present disclosure, changing on various forms and details can be made
Become.
Industrial feasibility
It can be applied to the system of domestic air conditioning or air conditioning for automobiles according to the austenitic stainless steel of the embodiment of present disclosure
Refrigerant tube.
Claims (9)
1. a kind of austenitic stainless steel with excellent resistance to tangerine peel, wherein including the flat of surface microstructure in the first region
Equal crystallite dimension Gs relative to the ratio between the average grain size Gi comprising internal grain in the second area Gs/Gi be 0.5 or
Smaller, the first area correspond to the overall thickness on the surface of austenitic stainless steel described in the distance of the austenitic stainless steel
10% or smaller depth, the second area correspond to austenitic stainless steel described in the distance than the austenitic stainless steel
10% deeper depth of the overall thickness on surface.
2. austenitic stainless steel according to claim 1, it includes the silicon (Si) of 0.1 weight % to 0.65 weight %, 1.0
The manganese (Mn) of weight % to 3.0 weight %, the nickel (Ni) of 6.5 weight % to 10.0 weight %, 16.5 weight % to 18.5 weights
Measure the chromium (Cr), 6.0 weight % or the less copper (Cu), 0.13 weight % of (than 0) or the less carbon of (than 0) of %
(C) and nitrogen (N) and iron (Fe) and other inevitable impurity.
3. austenitic stainless steel according to claim 1, wherein the average grain size Gs of the surface microstructure is 100 μm
Or smaller.
4. austenitic stainless steel according to claim 1 is manufactured by band casting.
5. austenitic stainless steel according to claim 4, wherein when the austenitic stainless steel by band casting come when casting,
It is 5 weight % or more to solidify the delta ferrite phase content retained later.
6. austenitic stainless steel according to claim 5, wherein the delta ferrite of the cold rolling microstructure of the austenitic stainless steel
Phase content is 0.5 weight % or more.
7. it is a kind of by make stainless steel across a pair of of rotating roller so that the stainless steel be frozen into the belt casting process of solid come
The method for manufacturing the austenitic stainless steel with excellent resistance to tangerine peel, the method includes：
Cast austenitic stainless, and to retain after solidification according to the element of formula (1) the control austenitic stainless steel
The content Δ of delta ferrite phase be 5 weight % or more, to manufacture hot rolled steel plate：
Δ=((Cr+Mo+1.5Mn+0.5Nb+2Ti+18)/(Ni+0.3Cu+30* (C+N)+0.5Mn+36)+0.262) × 161-
161, formula (1)
Wherein the symbol of element of formula (1) indicates the weight percent (weight %) of respective element.
8. according to the method described in claim 7, the wherein described austenitic stainless steel include 0.1 weight % to 0.65 weight %'s
Silicon (Si), the manganese (Mn) of 1.0 weight % to 3.0 weight %, the nickel (Ni) of 6.5 weight % to 10.0 weight %, 16.5 weight %
(zero is removed to the chromium (Cr) of 18.5 weight %, the copper (Cu) of 6.0 weight % or less (than 0), 0.13 weight % or less
Except) carbon (C) and nitrogen (N) and iron (Fe) and other inevitable impurity.
9. according to the method described in claim 7, it further includes being heat-treated to the hot rolled steel plate, then with 50% or more
High total reduction carries out cold rolling to the hot rolled steel plate, thus manufactures cold-rolled steel sheet,
The delta ferrite phase content of the cold rolling microstructure of the wherein described cold-rolled steel sheet is 0.5 weight % or more.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020150158665A KR20170056047A (en) | 2015-11-12 | 2015-11-12 | Austenitic stainless steel having exceelent orange peel resistance and method of manufacturing the same |
| KR10-2015-0158665 | 2015-11-12 | ||
| PCT/KR2016/012874 WO2017082631A1 (en) | 2015-11-12 | 2016-11-09 | Austenitic stainless steel having excellent orange peel resistance and manufacturing method therefor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN108348990A true CN108348990A (en) | 2018-07-31 |
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ID=58695848
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| CN201680065899.2A Pending CN108348990A (en) | 2015-11-12 | 2016-11-09 | Austenitic stainless steel and its manufacturing method with excellent resistance to tangerine peel |
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| Country | Link |
|---|---|
| US (1) | US20180371575A1 (en) |
| JP (1) | JP2018536089A (en) |
| KR (1) | KR20170056047A (en) |
| CN (1) | CN108348990A (en) |
| WO (1) | WO2017082631A1 (en) |
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|---|---|---|---|---|
| KR102419898B1 (en) * | 2017-06-26 | 2022-07-12 | 엘지전자 주식회사 | Gas heat pump system |
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2017082631A1 (en) | 2017-05-18 |
| KR20170056047A (en) | 2017-05-23 |
| JP2018536089A (en) | 2018-12-06 |
| US20180371575A1 (en) | 2018-12-27 |
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