CN102639742A - Austenite stainless steel sheet and method for producing same - Google Patents

Austenite stainless steel sheet and method for producing same Download PDF

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Publication number
CN102639742A
CN102639742A CN2010800523682A CN201080052368A CN102639742A CN 102639742 A CN102639742 A CN 102639742A CN 2010800523682 A CN2010800523682 A CN 2010800523682A CN 201080052368 A CN201080052368 A CN 201080052368A CN 102639742 A CN102639742 A CN 102639742A
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steel plate
stainless steel
construction
austenite
temper rolling
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CN102639742B (en
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泽田正美
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Nippon Steel Corp
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Sumitomo Metal Industries Ltd
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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
    • 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
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Abstract

Disclosed is an austenite stainless steel sheet for springs, which exerts both high strength and excellent moldability, and which has a chemical composition comprising 0.01 to 0.15% of C, 3.0% or less of Si, 3.0% or less of Mn, 10.0 to 30.0% of Cr, 4.0 to 20.0% of Ni, and 0.4% or less of N, the remainder being Fe or impurities, wherein the austenite content ([gamma]s) (%) of the surface of the steel sheet and the austenite content ([gamma]c) (%) of the plate thickness center is ([gamma]s+[gamma]c)/2<=55 and [gamma]s/[gamma]c>=0.1, and the remainder has a metal structure which is mainly a strain-induced martensite structure.

Description

Austenite stainless steel plate and method of manufacture thereof
Technical field
The present invention relates to austenite stainless steel plate and method of manufacture thereof, more specifically, relate to have HS and excellent formability concurrently spring with austenite stainless steel plate and method of manufacture thereof.
Background technology
For the spring material that uses as leaf spring, spring, housing, disk spring, elastic sheet switch (dome switches) etc. in electron device, atomic power device, the trolley part etc., the formability of the HS that requires to have the thin-walled property that is used to realize raw material and the excellence of the article shape that is used to be processed into regulation.
The material that is applicable to these purposes so far is that the SUS301 (AISI301) that belongs to the quasi-steady austenite stainless steel is a stainless steel.SUS301 is that martensite is brought out in the processing that stainless steel variant part when cold working becomes hard mutually, therefore, can more easily obtain HS; And; Because TRIP (phase change induction plasticity) effect can suppress local deformaton, therefore, also can obtain excellent formability.This spring material for example is disclosed in following patent documentation 1 ~ 3.
The excellent stainless steel of a kind of forming process property is disclosed in the patent documentation 1; It is following (in this manual that it contains C:0.03%; Unless otherwise prescribed; " % " relevant with chemical constitution is meant " quality % "), below the Si:1.0%, below the Mn:2.5%, Ni:4.0 ~ 10.0%, Cr:13.0 ~ 20.0%, N:0.06 ~ 0.30%, below the S:0.01%, below the O:0.007%, M value=330-(480 * C)-(2 * Si)-(10 * Mn)-(14 * Ni)-(5.7 * Cr)-(320 * N) is more than 30.
The stainless steel of the excellent in fatigue characteristics of a kind of spring characteristic and processing portion is disclosed in the patent documentation 2; It contains below the C:0.08%, below the Si:3.0%, below the Mn:4.0%; Ni:4.0 ~ 10.0%, Cr:13.0 ~ 20.0%, N:0.06 ~ 0.30%, below the O:0.007%, said M value is more than 40.
The stainless steel of a kind of forming process property and excellent in fatigue characteristics is disclosed in the patent documentation 3; It contains below the C:0.03%, Si: surpass 1.0% and 3.0% below, below the Mn:4.0%, Ni:4.0 ~ 10.0%, Cr:13.0 ~ 20.0%, below the N:0.30%, S:0.01% is following, below the O:0.007%, above-mentioned M value is in 30 ~ 100 scope.
Disclosed stainless steel all carries out cold rolling after the hot rolling with the calendering rate more than 50% in the patent documentation 1 ~ 3; Implement the final annealing of lesser temps and short period of time then; Make to generate the uniform recrystallize grain of refinement below the average crystalline particle diameter 10 μ m, make through temper rolling at last.That is, they all are that to utilize the little strengthening mechanism of formability deterioration be the strength characteristics that grain refining obtains to stipulate.Yet, in recent years,, therefore, can make the desired intensity of goods insufficient when using in the patent documentation 1 ~ 3 disclosed stainless steel because the intensity that spring material is required increases.
Disclosing a kind of SUS301L with low C, high N in the following patent documentation 4 is the high-strength spring material of substrate; Particularly; Open: to have below the C:0.03%, below the Si:1.0%, below the Mn:2.0%, Cr:16.0 ~ 18.0%, Ni:6.0 ~ 8.0%, below the N:0.25%, the chemical constitution of Nb:0 ~ 0.30% and have by be 50% or more in the recrystallize grain below the area occupation ratio median size 5 μ m and be lower than 100% with non-recrystallization partly for surpassing the stainless steel of the tissue that constitutes below 0% and 50%, implementing the temper rolling of draft more than 30%, to obtain, have area occupation ratio be that martensite and remainder are the stainless steel of austenitic polyphase structure or martensite single phase structure more than 40%.
In the patent documentation 4 disclosed stainless steel through temper rolling form contain processing and bring out the metal structure of martensitic stucture after, be shaped to the shape of regulation, further carry out ageing treatment, thereby fine chromium based nitride separated out on martensite.Through utilizing the precipitation strength of this moment, can under the situation that does not increase new process, realize high strength.
The prior art document
Patent documentation
Patent documentation 1: japanese kokai publication hei 4-214841 communique
Patent documentation 2: japanese kokai publication hei 5-279802 communique
Patent documentation 3: japanese kokai publication hei 5-117813 communique
Patent documentation 4: No. 4321066 specification sheets of japanese
Summary of the invention
Yet,, now spring material is also required the raising of further high strength and formability for the miniaturized that realizes goods, the raising of performance.Therefore, even disclosed stainless steel in the patent documentation 4 can not fully satisfy the desired performance of up-to-date goods sometimes.
An aspect; The invention provides a kind of austenite stainless steel plate; It is characterized in that; It has contain below C:0.01 ~ 0.15%, Si:3.0%, below the Mn:3.0%, Cr:10.0 ~ 30.0%, Ni:4.0 ~ 20.0%, below the N:0.40% and the chemical constitution that constitutes by Fe and impurity of remainder; And have following metal structure: the Ovshinsky scale of construction γ c (%) of the Ovshinsky scale of construction γ s (%) of surface of steel plate portion and the thickness of slab central part of steel plate satisfies (γ s+ γ c)/2≤55 and γ s/ γ c>=0.10, and remainder is mainly processing and brings out martensitic stucture.
Wherein, the austenitic volume fraction (%) that contained being meant from the surface of steel plate to the zone (being called surface of steel plate portion) of the depth location of thickness of slab direction 10 μ m of the Ovshinsky scale of construction γ s (%) of surface of steel plate portion.On the other hand, the austenitic volume fraction (%) that contains being meant from half the surface that forms of a face of steel plate being ground to original thickness of slab through mechanical mill and chemical grinding to the zone (thickness of slab central part) of the position of the thickness of slab direction 10 μ m degree of depth of the Ovshinsky scale of construction γ c (%) of thickness of slab central part.
In austenite stainless steel plate of the present invention, above-mentioned chemical constitution comprises that further following one-tenth assigns to replace a part of Fe:
1) at least a with below the Cu:3.0% below the Mo:3.0%; And/or
2) by below the Ti:0.50%, below the Nb:0.50% and select in the group that constitutes below the V:1.0% one or more.
On the other hand; The present invention is a kind of method of manufacture of austenite stainless steel plate; It is characterized in that, the steel raw material with above-mentioned chemical constitution is carried out hot rolling after, to the hot-rolled steel sheet that obtains carry out cold rolling and annealing; Form cold rolled annealed material, the road number of times above with draft (%)/10 carries out temper rolling to this cold rolled annealed material.
In aforesaid method, the average crystalline particle diameter of the austenite crystal of the cold rolled annealed material before the temper rolling is preferably below the 5 μ m.
According to the present invention, the austenite stainless steel plate and the method for manufacture thereof of the formability that has HS and excellence concurrently can be provided.
Description of drawings
The explanatory view of one example of the treatment process of behind temper rolling, being accepted for austenite stainless steel plate of the present invention shown in Figure 1.
Shown in Figure 2 is that the Ovshinsky scale of construction behind the temper rolling is at the explanatory view of an example of the relation of the distribution of thickness of slab direction and formability.
Shown in Figure 3 is the explanatory view of formability evaluation assessment.
Embodiment
Illustrate in greater detail the present invention with reference to accompanying drawing.
Austenite stainless steel plate of the present invention is to implement temper rolling and the cold-rolled steel sheet that forms.As shown in Figure 1, this austenite stainless steel plate is implemented forming process and is formed the shape of expectation behind temper rolling, implement ageing treatment then as required, is made into goods (for example various spring).
The inventor recognizes, through making the content increase as the C of solution strengthening element, is reinforced thereby make the processing that generates in the temper rolling bring out martensitic stucture, realizes the high strength of steel.The problem of above-mentioned undercapacity through will increasing the martensitic phase due to its C content reinforcement and further utilize Cr 2The precipitation strength of N is carried out overlapping and is resolved.
At this moment, martensite volume is few, austenite is residual many, the intensity that then can not obtain to stipulate if processing is brought out.Therefore, with the MV of the Ovshinsky scale of construction γ c (%) of the Ovshinsky scale of construction γ s (%) of surface of steel plate portion and thickness of slab central part promptly the value of (γ s+ γ c)/2 (following this value is called the average Ovshinsky scale of construction) be set at below 55.γ s and γ c are like above definition.
The inventor also recognizes, in order to improve because of high strength causes the formability that descends, it is effective that the thickness of slab direction of the control Ovshinsky scale of construction distributes.Shown in Figure 2 is that the Ovshinsky scale of construction behind the temper rolling is at the explanatory view of an example of the relation of the distribution of thickness of slab direction and formability.
As shown in Figure 2, even the average Ovshinsky scale of construction behind the temper rolling is identical,, can significantly improve formability through the distribution of the Ovshinsky scale of construction behind the change temper rolling in the thickness of slab direction.Particularly; Through the residual Ovshinsky scale of construction of surface of steel plate portion behind the increase temper rolling, thereby martensitic transformation is brought out in the maximum surface of steel plate portion generation processing of distortion when forming process after this, brings into play sufficient TRIP effect; Thus, can obtain excellent formability.
In addition, when this austenite stainless steel is carried out ageing treatment, be the center with the little martensitic phase of N solid solubility limit, and fine Cr 2N separates out, and therefore can also effectively utilize ageing strengthening.Like this, austenite stainless steel of the present invention can have HS and excellent formability concurrently.
On the other hand; The draught of each passage is big more, and the processing heating of the steel plate during temper rolling increases more, therefore; Surface temperature through rolling oil refrigerative steel plate is compared remarkable decline with the temperature of thickness of slab central part; When the calendering of following a time, the martensite volume that generates along with surface of steel plate enlarges markedly, and causes the Ovshinsky scale of construction of surface of steel plate portion significantly to reduce.
Promptly; When carrying out temper rolling with less road number of times like previous methods; The residual Ovshinsky scale of construction of surface of steel plate is compared remarkable minimizing with the residual Ovshinsky scale of construction of thickness of slab central part; When forming process after this, do not obtain austenitic processing bring out martensitic transformation with sufficient TRIP effect, formability descends.
To this, if increase the road number of times of temper rolling, reduce the draught of each passage, suppress the processing heating, then can increase the residual Ovshinsky scale of construction of surface of steel plate portion behind the temper rolling.Thus, in forming process after this, can reach of the distribution of the ideal Ovshinsky scale of construction in the thickness of slab direction.
Particularly; If can reach the thickness of slab direction of the Ovshinsky scale of construction that the Ovshinsky scale of construction γ c (%) of Ovshinsky scale of construction γ s (%) and the thickness of slab central part of the surface of steel plate portion behind the temper rolling satisfies the condition of γ s/ γ c >=0.10 distributes; Then the maximum surface of steel plate portion of distortion brings into play sufficient TRIP effect during after this forming process, and formability improves.
Even increase temper rolling the road number of times, reduce the draught of each passage; Because surface of steel plate portion temperature is lower than the thickness of slab central part; So compare with the thickness of slab central part, the martensitic growing amount of surface of steel plate portion is more, thereby the austenite quantitative change is got still less.Yet, be more than 1/10 of the Ovshinsky scale of construction of thickness of slab central part if distinguished the Ovshinsky scale of construction of surface of steel plate portion, in practicality, can guarantee sufficient formability.
As above illustrated, the present invention is based on following technical conceive: " seek to have concurrently the reinforcement through will increasing the martensitic phase due to the C content and utilize Cr 2Overlapping and the significantly high strength realized of precipitation strength due to the N, obtain excellent formability with the optimizing of utilizing the Ovshinsky scale of construction to distribute in the thickness of slab direction; Thus, can obtain to satisfy austenite stainless steel plate as the raw-material requirement of spring members of miniaturization and.
Chemical constitution, metal structure and the method for manufacture of austenite stainless steel plate of the present invention then, are described.
(1) chemical constitution
C:0.01~0.15%
C is the solution strengthening element, is extremely effective in the reinforcement of the martensitic phase that it generates in cold working, therefore, C content is set at more than 0.01%.Yet C measures when too much, in manufacturing processed, generates thick carbide, and therefore formability, erosion resistance deterioration are set at C content below 0.15%.C content is preferably more than 0.03%.
Below the Si:3.0%
Si is the solution strengthening element, and it helps the high strength of steel, and the deoxidation material during simultaneously also as melting uses.Yet, when Si content is too much, in manufacturing process, generating thick Si compound, these thick Si compounds cause hot workability and cold-workability deterioration.Therefore, Si content is below 3.0%, to be preferably below 2.8%.
Below the Mn:3.0%
The deoxidation material of Mn during as melting uses.In addition, Mn is an austenite stabilizer element, considers to contain Mn in right amount with the balance of other elements.Yet, when Mn content is too much, in manufacturing processed, generating thick Mn compound, thick Mn compound becomes the destructive starting point, the formability variation.Therefore, Mn content is below 3.0%, to be preferably below 2.8%.
Cr:10.0~30.0%
Cr is stainless fundamental element, through containing the Cr more than 10.0%, on the surface of steel, forms the passivation epithelium, and performance improves the effect of erosion resistance.In addition, when steel is carried out ageing treatment, because with fine Cr 2The form of N is separated out, and helps to improve the intensity of steel.Yet because Cr is the ferrite generting element, thereby Cr content at high temperature generates the δ ferrite, the remarkable deterioration of the hot workability of steel when too much.Therefore, Cr content is more than 10.0% and below 30.0%, is preferably more than 12.0% and below 25.0%.
Ni:4.0~20.0%
Ni is the fundamental element of austenite stainless steel, at room temperature to have excellent intensity-ductility equilibrated austenite phase in order stably obtaining, and to contain the Ni more than 4.0%.Yet when Ni content was too much, austenite was too stable mutually, suppressed processing and brought out martensitic transformation, therefore can not obtain HS.Therefore, Ni content is more than 4.0% and below 20.0%, is preferably more than 4.5% and below 18.0%.
Below the N:0.40%
N and C are the solution strengthening element equally, help to improve the intensity of steel.In addition, when steel is carried out ageing treatment, even with fine Cr 2The form of N is separated out, and also helps the high strength of steel.Yet, when N content is too much, brings out the limit during hot-work easily and split (Edge Cracking).Therefore, N content is below 0.40%, is preferably more than 0.05% and below 0.030%.
Austenite stainless steel of the present invention can further contain following optional interpolation element as required.
Below the Mo:3.0% with below the Cu:3.0% in one or both
Mo and Cu all make fine intermetallic compound separate out when ageing treatment, are the elements that helps the intensity rising of steel plate, therefore can contain Mo and Cu as required.Yet, because Mo content or Cu content when too much, at high temperature generate the δ ferrite easily, and on crystal boundary, separate out, so make the remarkable deterioration of hot workability sometimes.Therefore, Mo content, Cu content are below 3.0%, preferably are below 2.8%.
By below the Ti:0.5%, below the Nb:0.5% and select in below the V:1.0% one or more
Ti, Nb and V separate out with the form of fine carbide or nitride in manufacturing processed; Suppress the crystalline grain growing through pinning effect; In addition, help the intensity of steel plate to raise, therefore also can contain Ti, Nb and V as required through precipitation strength.Yet, when the content of these elements is too much, generating thick carbide, nitride, the destruction starting point when they become distortion makes the remarkable deterioration of formability.Therefore, Ti content and Nb content are set at below 0.5%, and V content is set at below 1.0%.Preferred Ti content and Nb content are below 0.4%, and preferred V content is below 0.8%.
Remainder except above-mentioned points is Fe and impurity.As representative impurity, can give an example out below the P:0.05%, S:0.03% is with inferior.
(2) metal structure
[austenite on the thickness of slab direction distributes]
The inventor has implemented multiple test; The result finds; The Ovshinsky scale of construction γ s (%) of surface of steel plate portion and the Ovshinsky scale of construction γ c (%) of thickness of slab central part satisfy following formula (1) and formula (2); Remainder is mainly to be processed when bringing out martensitic stucture, can obtain to have concurrently the austenite stainless steel plate of HS and formability.
Formula (1): (γ s+ γ c)/2≤55
Formula (2): γ s/ γ c >=0.10
At first; Shown in (1); Through will being that the average Ovshinsky scale of construction is set at below 55%, and make remainder be mainly high-intensity processing to bring out martensite, thereby can obtain high-intensity steel as the MV of the Ovshinsky scale of construction γ c of the Ovshinsky scale of construction γ s of surface of steel plate portion and thickness of slab central part.The average Ovshinsky scale of construction is preferably below 50%, more preferably below 45%, further is preferably below 40%, most preferably is below 35%.To the not special restriction of the lower limit of the average Ovshinsky scale of construction, when austenite is few, can not obtain sufficient TRIP effect at surface of steel plate during forming process, therefore be preferably more than 5%, more preferably more than 7.5%.
Then; Shown in (2); The Ovshinsky scale of construction γ s of surface of steel plate portion is set at more than 0.10 with the ratio of the Ovshinsky scale of construction γ c of thickness of slab central part (γ s/ γ c ratio); Thus, though when the forming process of plate, receive the surface of steel plate of maximum distortion also can give full play to austenitic processing bring out martensitic transformation with the TRIP effect, obtain excellent formability.γ s/ γ c ratio is preferably more than 0.2, more preferably more than 0.3, further is preferably more than 0.5, most preferably is more than 0.6.
In the present invention, the Ovshinsky scale of construction of surface of steel plate portion and the Ovshinsky scale of construction of thickness of slab central part satisfy formula (1) and formula (2) simultaneously, thereby can have HS and excellent formability concurrently.
Remainder beyond the austenite of metal structure mainly brings out martensitic phase by processing and constitutes.This processing is brought out martensite and is generated through the annealed steel plate being carried out temper rolling after cold rolling.Therefore, austenite stainless steel plate of the present invention is the temper rolling material.
" mainly bringing out martensitic phase by processing constitutes " is meant that processing brings out more than the 50 volume % that martensite accounts for the remainder except that austenite.In the austenite stainless steel plate according to following method manufacturing of the present invention; Metal structure is that martensite is brought out in austenite and processing basically; As phase in addition, the fine precipitate of can giving an example out (carbide, nitride, carbonitride) etc., but it is a trace.The complete martensite single phase structure of γ s=γ c=100% is not within object of the present invention.
As stated, because the Ovshinsky scale of construction at the thickness of slab central part more than surface of steel plate portion, so even in the austenite stainless steel plate of the present invention that the Ovshinsky scale of construction of surface of steel plate portion has improved, γ s < also set up by the relation of γ c (be γ s/> γ c < 1).
The crystal particle diameter of the austenite crystal before the temper rolling: below the 5 μ m
Grain refining is known as the little enhancement method of steel deteriorated ductility, also is effective enhancement method for the present invention as the stainless steel of object.In addition,, improve the density of crystal boundary, disperse, suppress the effect that crackle produces thereby also have the strain that concentrates on crystal boundary when making forming process through reducing crystal particle diameter.Therefore, in the present invention, the crystal particle diameter of the austenite crystal of the steel plate (cold rolled annealed material) before the temper rolling is preferably set to below the 5 μ m.
(3) method of manufacture
According to the present invention; After steel raw material with above-mentioned chemical constitution carried out hot rolling; Carry out cold rolling and annealing to the hot-rolled steel sheet that obtains; Form cold rolled annealed material, the road number of times above with draft (%)/10 carries out temper rolling to this cold rolled annealed material, thereby can make the austenite stainless steel plate of the invention described above.
Hot rolling, cold rolling and annealing all can implement according to ordinary method.Cold rolling preferably carrying out about 1 ~ 3 time makes that total draft is about 30 ~ 90%.When obtaining total draft of regulation, anneal.Can also implement the cold rolling of multi-pass and annealing repeatedly.To the not special restriction of the cold rolling road number of times of implementing before the temper rolling.
Increase the total draft after cold rolling, when forming the average crystalline particle diameter that supplies to austenite crystal follow-up temper rolling, cold rolled annealed material and be metal structure fine below the 5 μ m, especially formability becomes well, so is preferred.
[temper rolling condition]
In the present invention, bring out the reinforcement that martensite carries out, strengthen carrying out temper rolling in order to utilize to greatest extent through processing.Total draft is preferably more than 40%, more preferably more than 50%, most preferably is more than 60%.The not special restriction of the upper limit of total draft is usually less than 100%, is preferably below 90%.
When carrying out the enhanced temper rolling with few road number of times like this; As stated; Martensite is brought out in the processing of surface of steel plate portion to be increased; The Ovshinsky scale of construction of this part reduces, and can not satisfy the Ovshinsky scale of construction γ s of surface of steel plate portion and the ratio of the Ovshinsky scale of construction γ c of thickness of slab central part (γ s/ γ c ratio) >=0.1, formability deterioration.
The relation that road number of times when the inventor has investigated temper rolling and the austenite on the thickness of slab direction distribute; Consequently; Confirm: shown in (3),, be more than 0.10 thereby make γ s/ γ c ratio through carrying out temper rolling with the above road number of times of total draft (%)/10.Therefore, implement temper rolling with the above road number of times of the total draft (%)/10 in the temper rolling.For example, total draft of temper rolling is 65% o'clock, and the road number of times is more than 7.
Formula (3): the total draft of temper rolling road number of times >=temper rolling (%)/10
The draft of each passage of preferred surface dress rolling is roughly the same.Therefore, preferably making the draft of each passage of temper rolling is below 10%.Owing to exceedingly increase number of times operating efficiency is worsened, therefore, the road number of times is preferably set to the minimum passage that satisfies total draft (%)/10 and counts to than it and many in the scope of road number of times of 2 passages.
Embodiment 1
The stainless chemical ingredients of using in this example has been shown in the table 1.Steel A ~ F is the steel of the present invention that satisfies the composition of the present invention's regulation, and steel G ~ M is the comparative steel of the composition of discontented unabridged version invention regulation.
Creating conditions and test-results of steel plate that use steel A ~ M makes has been shown in the table 2.Steel plate 1 ~ 8th satisfies the steel plate that the present invention stipulates, steel plate 9 ~ 18 is the comparison steel plate of discontented unabridged version invention regulation.
With the steel melting that common atmosphere melting furnace will have the chemical constitution shown in the table 1, form the bloom of 17kg.This bloom is implemented hot rolling and annealing, behind the hot-rolled steel sheet of formation thickness 6.0mm, this hot-rolled steel sheet is carried out 1 ~ 3 cold rolling and annealing repeatedly, obtain the cold rolled annealed material of thickness 0.8 ~ 4.0mm.Temper rolling to this cold rolled annealed material enforcement multiple tracks number of times finally forms thickness of slab 0.4mm thin plate, under the equal condition of the draft of each passage, carries out temper rolling.
The test film that use is gathered from the steel plate before and after this temper rolling is with following method investigation crystal particle diameter, the Ovshinsky scale of construction, formability, tensile strength.In addition, a part of steel plate is implemented 1 minute ageing treatment under 300 ℃ behind temper rolling.Value after the tensile strength Use Limitation of these steel plates is handled.
(the average crystalline particle diameter after the annealing)
Scan microscope photo after the crystal particle diameter of austenite crystal is corroded by the test film cross section cold rolled annealed acquired for materials before temper rolling calculates by the nominal particle size of austenite crystal.
(the Ovshinsky scale of construction)
The surface of steel plate portion of the test film that the steel plate of calculating after by temper rolling obtains and through mechanical mill and chemical grinding the Ovshinsky scale of construction on the thickness of slab central part surface of grinding.Use during calculating through the integrated intensity ratio of X-ray diffraction mensuration and the scan microscope photo after the etching.In table 2, the austenite scale of surface of steel plate portion is shown γ s, and the austenite scale on thickness of slab central part surface is shown γ c.
(formability)
Shown in Figure 3 is the explanatory view of formability evaluation assessment.The square test film of 100mm to the steel plate behind temper rolling is gathered is implemented shallow stretching (shallow drawing) processing as shown in Figure 3.After this, use the observation by light microscope bight, confirming does not have crackle then to be evaluated as ◎ fully, and confirming does not have the successive crackle then to be evaluated as zero, confirm to successive crackle or fracture then be evaluated as *.
(tensile strength)
Tensile strength is used the JIS-13B tension test sheet of being gathered by the steel plate after modulation calendering back or the ageing treatment, measures according to JISZ 2241.Tensile strength surpasses 1500N/mm 2Be shown zero, do not reach 1500N/mm 2Be shown *, be shown in the table with measured value.
[table 1]
Figure BDA00001656197100131
Notes) underscore is illustrated in beyond the scope of the present invention.
[table 2]
Figure BDA00001656197100141
Notes) underscore is illustrated in beyond the scope of the present invention.
Steel plate 1 ~ 8 in the table 2 is steel plate of the present invention, has excellent formability and HS.In addition, through steel plate 1,2 is compared, thereby confirm: because the fine Cr during ageing treatment 2Separating out of N and can obtain extra high intensity.In addition, the crystal particle diameter after can confirming to anneal is that steel plate 3,4 below the 5 μ m can obtain extra high intensity and excellent formability.
Steel plate 9 ~ 18th, chemical constitution or create conditions depart from the comparative example of the scope of the present invention's regulation.
The γ s/ γ c of steel plate 9 ~ 11 is lower than 0.1, though can obtain HS, formability is bad.In addition; When steel plate 7 compares with steel plate 11 with steel plate 10 or steel plate 8; Steel plate 7,8 has HS and formability concurrently, though HS is arranged steel plate 10,11 but formability is bad, can confirm thus: even make the steel of identical component with identical temper rolling rate; The distribution of the Ovshinsky scale of construction also can be because of calendering road number of times changes, and characteristic variations is also bigger.
The C content and the N content of steel plate 12 are higher than scope of the present invention, generated thick carbonitride, so formability are significantly bad.
The C content of steel plate 13 is lower than scope of the present invention, even intensity is also very little after ageing treatment.In addition, because γ s/ γ c is lower than 0.1, so formability is also bad.
Cr content, the Ni content of steel plate 14 are higher than scope of the present invention, and the MV of γ s/ γ c surpasses 55, though therefore after ageing treatment intensity also very low.
Cr content, the Ni content of steel plate 15 are lower than scope of the present invention, and γ s/ γ c is lower than 0.1, so formability is bad.
Si content, the Mn content of steel plate 16 are higher than scope of the present invention, and the MV of γ s and γ c surpasses 55, though therefore after ageing treatment intensity also low.In addition, generated thick Si compound, Mn compound, formability is also bad.
Mo content, the Cu content of steel plate 17 are higher than scope of the present invention, and the MV of γ s and γ c surpasses 55, though therefore after ageing treatment intensity also low.In addition, generated thick intermetallic compound, formability is also bad.
In addition, the Ti content of steel plate 18 is higher than scope of the present invention, has generated thick TiN, and formability is bad.

Claims (5)

1. austenite stainless steel plate; It is characterized in that; It has contain in below quality % C:0.01 ~ 0.15%, Si:3.0%, below the Mn:3.0%, Cr:10.0 ~ 30.0%, Ni:4.0 ~ 20.0%, below the N:0.40% and the chemical constitution that constitutes by Fe and impurity of remainder; And have following metal structure: the Ovshinsky scale of construction γ s (%) of surface of steel plate portion and the Ovshinsky scale of construction γ c (%) of thickness of slab central part satisfy (γ s+ γ c)/2≤55 and γ s/ γ c>=0.10, and remainder is mainly processing and brings out martensitic stucture.
2. austenite stainless steel plate according to claim 1, said chemical constitution have at least a below the quality % Mo:3.0% or below the Cu:3.0% and replace a part of Fe.
3. austenite stainless steel plate according to claim 1 and 2, said chemical constitution have in quality % by below the Ti:0.50%, below the Nb:0.50% and select in the group that constitutes below the V:1.0% one or more replace a part of Fe.
4. the method for manufacture of each described austenite stainless steel plate in the claim 1 ~ 3; It is characterized in that; After steel raw material with said chemical constitution carried out hot rolling; Carry out cold rolling and annealing to the hot-rolled steel sheet that obtains, form cold rolled annealed material, the road number of times above with draft (%)/10 carries out temper rolling to this cold rolled annealed material.
5. method according to claim 4, wherein, the average crystalline particle diameter of the austenite crystal of the cold rolled annealed material before the temper rolling is below the 5 μ m.
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