CN105452505A - Austenitic stainless steel sheet and method for producing same - Google Patents

Austenitic stainless steel sheet and method for producing same Download PDF

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CN105452505A
CN105452505A CN201380078606.0A CN201380078606A CN105452505A CN 105452505 A CN105452505 A CN 105452505A CN 201380078606 A CN201380078606 A CN 201380078606A CN 105452505 A CN105452505 A CN 105452505A
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stainless steel
strain rate
steel plate
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CN105452505B (en
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泽田正美
安达和彦
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Nippon Steel Corp
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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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • 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
    • 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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Abstract

Provided is an austenitic stainless steel sheet which has a product of the 10% flow stress at a strain rate of 1000/s and the uniform elongation at a strain rate of 0.1/s of 450 MPa or more and also has high strength at a high strain rate and improved ductility at a low strain rate. An austenitic stainless steel sheet containing, in % by mass, 0.02 to 0.30% of C, 10.0 to 25.0% of Cr, 3.5 to 10.0% of Ni, 0 to 3.0% of Si, 0.5% to 5.0% of Mn, 0.10 to 0.40% of N, 0 to 3.0% of Mo, 0 to 3.0% of Cu, 0 to 0.10% of Ti, 0 to 0.50% of Nb and 0 to 1.0% of V, wherein the value determined by the following formula: C + 3 * N is 0.4% or more, and the remainder is made up by Fe and impurities. In the austenitic stainless steel sheet, the Md30 value which is defined by formula (1) is 0 to 50 DEG C inclusive, the volume ratio of each of a Cr carbide and a Cr nitride is 1% or less, and the average crystal particle diameter of a parent phase is 10 [mu]m or less.

Description

Austenite stainless steel plate and its manufacture method
Technical field
The present invention relates to austenite stainless steel plate and its manufacture method, austenite stainless steel plate that use in particular to the structural member being such as suitable as automobile, electric car etc., that taken into account the intensity in collision corresponding high strain rate region and the toughness in the corresponding low strain rate region of compression moulding and its manufacture method.
Background technology
In recent years, as the reply to environmental problem, expect that the fuel economy of automobile, railway etc. improves, as its solve scheme, the lightweight of car body is very effective.And then for the lightweight of car body, it is effective for forming the raw-material lightweight, the specifically raw-material thin-walled property that account for the most structural member of weight.But raw-material thin-walled property makes shock absorption ability when rigidity, collision reduce.Therefore, in recent years, particularly release high strength starting material are applied to structural member.
Such as, the front longitudinal etc. of automobile needs the apparatus with shock absorbing when there is not moderate finite deformation.As such index compared with the shock absorption ability in small strain region, consider that 10% stress of fluidity under the corresponding strain rate 1000/s of collision is suitable.In addition, as the index of compression moulding, the uniform elongation that consideration is suitable under the corresponding strain rate 0.1/s of compacting is suitable.That is, the material can saying 10% stress of fluidity under strain rate 1000/s and the uniform elongation excellence under strain rate 0.1/s is suitable as structural member.Specifically, expect 10% stress of fluidity under strain rate 1000/s and the uniform elongation under strain rate 0.1/s long-pending become more than 450MPa shock absorption ability and compression moulding in any one or both extremely excellent materials.
Patent Document 1 discloses following invention: add Mn in a large number, the phase transformation of processing strain induced martensite can not be caused when being out of shape, improve the austenite stainless steel of intensity due to austenitic twin distortion.But, in the austenite stainless steel of this invention, do not cause the phase transformation of processing strain induced martensite completely, therefore there is the situation that the harmony of gained intensity and elongation is insufficient.Specifically, in patent documentation 1, as embodiment, describe 10% stress of fluidity in dynamic tensile test and the elongation at break in static tensile test, long-pending all the resting on of the two is less than 400MPa.
Patent Document 2 discloses the invention of the automotive structural members austenite stainless steel of low Ni type.But the crystal particle diameter of the austenite stainless steel of this invention is thick to several 10 μm, therefore, when carrying out shaping as automotive structural members, mostly produce be full of cracks on the surface in bending machining portion, the characteristic as structural member is insufficient.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 2009-30128 publication
Patent documentation 2: Japanese Unexamined Patent Publication 2010-196103 publication
Summary of the invention
the problem that invention will solve
In order to the raising of the further lightweight of implementation structure component, design freedom, at present starting material are also required that the high strength under high strain rate and the toughness under low strain rate improve.Therefore, even if for by the austenite stainless steel disclosed in patent documentation 1,2, the performance required by up-to-date goods cannot sometimes also fully be met.
for the scheme of dealing with problems
The present inventor etc. are when taking into account high strength and high tenacity generally as contrary characteristic, have studied the gimmick of the various high strengths of steel, found that: by the gimmick of various high strength, effective utilization (a) based on the strengthening of solid solution C, solid solution N, (b) based on the strengthening of the phase change induction plasticity (TRIP effect) during distortion and (c) strengthening based on crystal grain miniaturization, thus the high strength under high strain rate can be taken into account and the high tenacity under low strain rate, thus complete the present invention.The present invention as described below.
[1]
A kind of austenite stainless steel plate, wherein, in mass %, C:0.02 ~ 0.30%, Cr:10.0 ~ 25.0%, Ni:3.5 ~ 10.0%, Si:0 ~ 3.0%, Mn:0.5% ~ 5.0%, N:0.10 ~ 0.40%, Mo:0 ~ 3.0%, Cu:0 ~ 3.0%, Ti:0 ~ 0.10%, Nb:0 ~ 0.50%, V:0 ~ 1.0%, C+3 × more than N:0.4%, surplus is made up of Fe and impurity, the Md specified by following (1) formula 30value is more than 0 DEG C and less than 50 DEG C, and the volume fraction of Cr carbide and Cr nitride is less than 1%, and the average crystal particle diameter of parent phase is less than 10 μm.
Md 30value (DEG C)=497462 (%C+%N)-9.2 (%Si)-8.1 (%Mn)-13.7 (%Cr)-20 (%Ni+%Cu)-18.5 (%Mo) (1)
[2]
Austenite stainless steel plate according to [1], wherein, in mass %, containing at least a kind in Mo:0.4 ~ 3.0%, Cu:0.4 ~ 3.0%.
[3]
Austenite stainless steel plate according to [1] or [2], wherein, in mass %, one kind or two or more containing what be selected from the group that is made up of Ti:0.01 ~ 0.10%, Nb:0.02 ~ 0.50%, V:0.02 ~ 1.0%.
[4]
Austenite stainless steel plate according to any one in [1] ~ [3], wherein, amassing as more than 450MPa of 10% stress of fluidity under strain rate 1000/s and the uniform elongation under strain rate 0.1/s.
[5]
A kind of manufacture method of austenite stainless steel plate, hot rolling is implemented to stainless steel starting material, then with the annealing temperature T (DEG C) and annealing time t (sec) that meet following (2) formula, hot-rolled sheet annealing is implemented to gained hot-rolled steel sheet, described stainless steel starting material in mass %, C:0.02 ~ 0.30%, Cr:10.0 ~ 25.0%, Ni:3.5 ~ 10.0%, Si:0 ~ 3.0%, Mn:0.5% ~ 5.0%, N:0.10 ~ 0.40%, Mo:0 ~ 3.0%, Cu:0 ~ 3.0%, Ti:0 ~ 0.10%, Nb:0 ~ 0.50%, V:0 ~ 1.0%, C+3 × more than N:0.4%, surplus is made up of Fe and impurity.
t×exp(-25007/(T+273))＞9.36991×10 -6···(2)
the effect of invention
10% stress of fluidity under the strain rate 1000/s of austenite stainless steel plate of the present invention and the uniform elongation under strain rate 0.1/s amass as more than 450MPa, significantly can improve any one or both in shock absorption ability and compression moulding compared with existing steel, the high strength under high strain rate can be realized and the toughness under low strain rate improves.
Accompanying drawing explanation
Fig. 1 is for illustrating the figure of (2) formula.
Fig. 2 is the figure of the analytical results that the hot-roll annealing plate utilizing EPMA X-ray analysis X is shown, (a) of Fig. 2 illustrates the analytical results of steel plate 3, (b) of Fig. 2 illustrates that the analytical results of steel plate 43, (c) of Fig. 2 illustrate the analytical results of steel plate 44.
Embodiment
The chemical constitution of austenite stainless steel plate of the present invention, metallographic structure and manufacture method are described.It should be noted that, in this specification sheets, as long as no being particularly limited to, then about " % " expression " quality % " of chemical constitution.
1. chemical constitution
(C：0.02～0.30％)
C is solution strengthening element, is greatly conducive to the high strength under high strain rate.Solution strengthening based on C is the strengthening of effectively having used short distance obstacle (Short-rangeobstacles), and the strain rate dependency of strengthening is large.Therefore, with the solution strengthening based on alloying element, the strengthening based on dislocation, other strengthening phase ratios based on precipitate, the deterioration of the toughness under low strain rate is little, is extremely effective for the high strength under the high strain rate as object of the present invention and taking into account of the toughness under low strain rate.Therefore, C content is set to more than 0.02%.But when C content is excessive, generate thick carbide in the fabrication process, the harmony deterioration of intensity and toughness, therefore, is set to less than 0.30% by C content.C content is preferably more than 0.04% and less than 0.30%, more preferably more than 0.06% and less than 0.30%.
(Cr：10.0～25.0％)
Cr is stainless fundamental element, by containing more than 10.0%, forms passivation overlay film and play the effect improving erosion resistance on the surface of steel.But when Cr content is excessive, at high temperature generate delta ferrite, the hot workability of steel is obviously deteriorated.Therefore, Cr content is set to more than 10.0% and less than 25.0%.Cr content is preferably more than 15% and less than 20%.
(Ni：3.5～10.0％)
Ni is the fundamental element of austenite stainless steel, in order to have under stably obtaining room temperature excellent intensity and toughness balanced austenite phase and containing more than 3.5% Ni.But when Ni content is too much, austenite is excessive stabilization mutually, and processing strain induced martensite phase transformation during distortion is suppressed, is difficult to work hardening, and result elongation reduces.Therefore, Ni content is set to more than 3.5% and less than 10.0%.Ni content is preferably more than 3.5% and less than 8%.
(Mn：0.5～5.0％)
Mn can use as deoxidation material during melting.In addition, Mn is austenite stabilizer element, and is improved the solid solubility limit of C, N, makes the effect of a large amount of C, N solid solutions, considers and the harmony of other elements and containing appropriate.But when Mn content is excessive, generate thick Mn compound in the fabrication process, thick Mn compound becomes the starting point of destruction, formability deterioration.According to above reason, Mn content is set to more than 0.5% and less than 5.0%.Mn content is preferably more than 1.0% and less than 5.0%, more preferably more than 1.5% and less than 5.0%.
(N：0.10～0.40％)
N and C is similarly solution strengthening element, is effective to the high strength under high strain rate.Solid solution N in the same manner as solid solution C with the solution strengthening based on alloying element, the strengthening based on dislocation, strengthening phase ratio based on precipitate, the deterioration of the toughness under low strain rate is little, therefore, it is extremely effective for improving the high strength under the high strain rate as object of the present invention and the toughness under low strain rate.Therefore, N content is set to more than 0.10%.But when N content is excessive, generate thick nitride in the fabrication process, the harmony deterioration of intensity and toughness, is therefore set to less than 0.40% by N content.N content is preferably more than 0.15% and less than 0.30%, more preferably more than 0.20% and less than 0.25%.
(C+3 × more than N:0.4%)
As described above, C, N are solution strengthening element, are greatly conducive to the high strength under high strain rate.Solution strengthening based on C and N and the solution strengthening based on alloying element, the strengthening based on dislocation, the ratio of the strengthening phase based on precipitate, the deterioration of the toughness under low strain rate is little, therefore, in order to take into account as the high strength under the high strain rate of object of the present invention and the toughness under low strain rate, C+3 × N is set to more than 0.4%.
Austenite stainless steel of the present invention can contain any Addition ofelements of following explanation as required further.
(Si：0～3.0％)
Si is solution strengthening element, is conducive to the high strength of steel, and also can use as deoxidation material during melting.Si can contain as required.In order to high strength, expect containing more than 0.1%.But when Si content is excessive, generate thick Si compound in the fabrication process, these thick Si compounds cause the deterioration of hot workability and cold-workability.Therefore, Si content is less than 3.0%, expects to be less than 2.8%.
(one or both in Mo:0 ~ 3.0% or Cu:0 ~ 3.0%)
Mo is to the effective element of the raising of erosion resistance, can contain as required.But, when Mo content is too much, cause the reduction of toughness, therefore Mo content is set to less than 3.0%.Mo content is preferably less than 2.5%, improves effect, preferably containing more than 0.4% to positively obtain erosion resistance.
The raising of Cu to cold-workability, toughness is effective, can contain as required.But, when Cu content is too much, bring out red brittleness, therefore Cu content is set to less than 3.0%.Cu content is preferably less than 2.5%, in order to positively obtain the raising effect of cold-workability, toughness, preferably containing more than 0.4%.
(be selected from Ti:0 ~ 0.10%, Nb:0 ~ 0.50% and V:0 ~ 1.0% one kind or two or more)
Ti, Nb and V all separate out with the form of fine carbide or nitride in the fabrication process, have the effect of the grain growing being suppressed crystal by pinning effect, therefore can contain as required.But when the content of these elements becomes excessive, generate thick carbide, nitride, destruction starting point when they become distortion, makes formability obviously deteriorated.Therefore, Ti content is set to less than 0.10%, Nb content is set to less than 0.50%, V content is set to less than 1.0%.Preferably, Ti content is less than 0.05%, Nb content is less than 0.2%, V content is less than 0.5%.In addition, in order to the effect of the grain growing of the crystal that is positively inhibited, preferably contain Ti, the Nb of more than 0.02%, the V of more than 0.02% of more than 0.01%.
Surplus is in addition to the foregoing Fe and impurity.As impurity, can enumerate: the material comprised in material contained in the starting material such as ore, waste material, manufacturing process.Representatively impurity, can enumerate: below P:0.05%, S:0.03% are such as the following.
(Md 30value is more than 0 DEG C and less than 50 DEG C)
Md 30value for representing the index of austenite stability, for apply 30% tension strain time, 50% become martensitic processing temperature mutually.Md 30value is specified by following (1) formula.By by Md 30value is set to more than 0 DEG C and less than 50 DEG C, thus suitably generates processing strain induced martensite when being out of shape, and embodies TRIP effect, therefore can obtain more excellent intensity and the harmony of toughness.
Md 30value (DEG C)=497-462 (%C+%N)-9.2 (%Si)-8.1 (%Mn)-13.7 (%Cr)-20 (%Ni+%Cu)-18.5 (%Mo) (1)
2. metallographic structure
(crystal particle diameter of austenite parent phase: less than 10 μm)
Known crystal grain fine turns to the little reinforcement of the toughness deterioration of steel, even if for being also effectively strengthen gimmick as the stainless steel of object in the present invention.In addition, by reducing crystal particle diameter, improve the density of crystal grain boundary, thus also have the strain dispersion making to concentrate on crystal grain boundary when being out of shape, the effect suppressing the generation of crackle.Therefore, the crystal particle diameter of austenite parent phase is set to less than 10 μm.The crystal particle diameter of austenite parent phase is preferably less than 7 μm, more preferably less than 6 μm.
(the volume fraction of Cr carbonitride: less than 1.0%)
As described above, by increasing C, N content, improve the harmony of the intensity under high strain rate and the toughness under low strain rate, this is because, when solid solution C, N, the strain rate dependency had an impact to high strength is large.Therefore, even if add C, N in a large number, they also exist with the form of Cr carbide, Cr nitride, therefore cannot obtain this effect.Herein, as Cr carbide, Cr can be enumerated 23c 6, as Cr nitride, can Cr be enumerated 2n, CrN.So-called Cr carbide comprises the Cr that solid solution has the N of trace herein 23(C, N) 6, Cr nitride comprises the Cr that solid solution has the C of trace 2(C, N), Cr (C, N).And then when there is compound thick as Cr carbide, Cr nitride, the interface of Cr carbide, Cr nitride itself or Cr carbide, Cr nitride and parent phase easily becomes the starting point of crackle, makes toughness obviously deteriorated.Therefore, expect that Cr carbide, Cr nitride are few, specifically, the volume fraction of Cr carbide and Cr nitride is set to less than 1.0%.
3. manufacture method
The invention is characterized in, by making a large amount of C, N solid solutions, obtaining excellent intensity and the harmony of toughness.But, such as disclosed in patent documentation 2, in the hot-rolled sheet annealing of 1080 DEG C, about 60 seconds, separate out when hot rolling or C, N not homogenizing fully of multiviscosisty, even if C, N of their precipitation or multiviscosisty are through follow-up solutionizing thermal treatment, annealing, sometimes also can remain, in process of cooling after solutionizing thermal treatment, annealing, to remain Cr carbide, the precipitate of nitride easily separates out as core, cannot form the state of solid solution a large amount of C, N.
The present inventor etc. have studied the diffusion of annealing temperature T (DEG C), annealing time t (sec) and C, N in great detail, result is distinguished: undertaken more than 150 μm by utilizing C, N in hot-rolled sheet and spread such annealing temperature T and annealing time t and implement hot-rolled sheet annealing, thus make to separate out when hot rolling or C, N abundant solid solution of multiviscosisty, homogenizing.
Herein, diffusion length λ, as (3) formula, utilizes diffusion coefficient D, time t arranges.And then, the diffusion coefficient D (m of the N in austenite stainless steel 2/ sec) according to document (such as, the physical property of steel and nitrogen < Steel physical property と Chisso >, the 69th page, AGNEGijutsuCenterInc.) by shown in (4) formula.
&lambda; = 2 D t ... ( 3 )
D = 0.0012 exp ( - 2.50073 &times; 10 4 T + 273 ) ... ( 4 )
Based on (3) formula and (4) formula, what arrange that N carries out that the conditions of more than 150 μm diffusions obtain is (2) formula.In addition, illustrate that the figure of (2) formula is Fig. 1.The part (upper right side part) scribbling grey in Fig. 1 is the scope meeting (2) formula.The spread coefficient of the C in austenite stainless steel is substantially identical with N, therefore, if carry out meeting the annealing temperature of (2) formula and the hot-rolled sheet annealing of annealing time, then C also fully spread, homogenizing.
t×exp(-25007/(T+273))＞9.36992×10 -6···(2)
In addition, when hot-rolled sheet is annealed, even if C, N spread, homogenizing, when speed of cooling is slow, in cooling, C, N also separate out with the form of Cr carbide, Cr nitride sometimes.Particularly preferably speed of cooling is set to 2.0 DEG C/more than sec, until 700 DEG C that Cr carbide, Cr nitride are easily separated out.Even if the solution process after hot-rolled sheet annealing, in annealing, also preferable temperature keeps with more than 900 DEG C, is set to 2.0 DEG C/more than sec from keeping the speed of cooling of temperature to 700 DEG C.
Embodiment
The piece of stainless steel of the 17kg of the chemical constitution shown in melting table 1.In table 1, steel grade A1 ~ A25 is chemical constitution, (C+3 × N) amount, Md 30value all meets the material of scope of the present invention, and steel grade B1 ~ B14 is chemical constitution, (C+3 × N) amount, Md 30at least 1 in value at extraneous material of the present invention.In table 1, "-" refers to, undesirably containing (content is less than the scope of expectation or is 0).
[table 1]
The hot rolling starting material that machining forms thickness 45mm are carried out to this stainless steel ingot bar.Afterwards, implement hot rolling, form the hot-rolled steel sheet of thickness 6.0mm, then with the annealing temperature shown in table 2 and annealing time, hot-rolled sheet annealing is implemented respectively to this hot-rolled steel sheet.Steel plate 28,34,35,43,44 does not meet the example of above-mentioned (2) formula for annealing temperature T (DEG C), the annealing time t (sec) in hot-rolled sheet annealing.
Afterwards, repeat cold rolling and anneal each 2 ~ 3 times, obtaining the cold-reduced sheet of thickness 1.0mm.Finally, the annealing of 180 seconds is implemented with 900 ~ 1000 DEG C.
10% stress of fluidity (10%FS) under the volume fraction V (%) of Cr carbonitride, average crystal particle diameter D (μm), strain rate 1000/s, the uniform elongation (UEL) under strain rate 0.1/s utilize following gimmick to measure.
(volume fraction of Cr carbonitride)
Steel plate is carried out chemical grinding until thickness of slab becomes 3/4, then characteristic X-ray is carried out X diffraction as Co-K alpha-ray, the scope that 2 θ is set to 30-100 (degree).Use the diffraction peak detected, calculate the volume fraction V of Cr carbide and Cr nitride.The X-ray diffraction peak of parent phase uses from (111) face of austenite phase, (200) face, (220) face and the diffraction peak from (110) face of the martensitic phase of parent phase, (200) face, (211) face.As the X-ray diffraction peak of carbide, use from Cr 23c 6(420) face, (422) face, (440) face diffraction peak, as the X-ray diffraction peak of nitride, use from Cr 2the diffraction peak in (111) face of (110) face of N, (002) face, (111) face and CrN, (220) face, (311) face.
Even if be the peak from phase homophase, also different according to the reflectivity of face different x-ray.Therefore, the integrated intensity at each peak carries out stdn by the relative intensity at each peak divided by JCPDS card.
In addition, when the constitution element of each phase is different, the atomic scattering factor (atomicscatteringfactor) of these constitution elements is different, and therefore the reflectivity of X-ray is different.But, according to the representational document measured about X-ray diffraction i.e. " B.D.Cullity:ElementsofX-rayDiffraction; 2nded.; Addison-Wesley; Massachussets; (1978) ", difference as the stainless parent phase of object and carbide, the principal element of nitride and the atomic scattering factor of Fe, Cr, Ni, Mn in the present invention is little, therefore, in the scope of this embodiment, the impact that the difference can ignoring the constitution element of each phase causes reflectivity.
According to more than, the volume fraction V of Cr carbide and Cr nitride is by shown in following (5) formula.V c, V n, V γ, V α 'value after being respectively the relative intensity divided by JCPDS card of the integrated intensity at the peak of each of Cr carbide, Cr nitride, austenite phase, martensitic phase, to this value summation gained.
V＝(V C+V S)/(V C+V N+V γ+V α′)···(5)
One is illustrated in (6) formula.Herein, I γ (hkl)for the integrated intensity at the peak from γ (hkl) face obtained in X-ray diffraction mensuration, RI γ (hkl)for the RI of JCPDS card γ (hkl)relative intensity.
V γ＝I γ(111)/RI γ(111)+I γ(200)/RI γ(200)+I γ(220)/RI γ(220)···(6)
(crystal particle diameter)
The rolling direction parallel cut of grinding steel plate, carries out nitric acid electrolytic corrosion, then takes metallographic structure with scan microscope.Using the nominal particle diameter that obtained by the captured photo average crystal particle diameter as parent phase.
(10% stress of fluidity under strain rate 1000/s, the uniform elongation under strain rate 0.1/s)
Tension test is carried out under strain rate 1000/s and 0.1/s.For each steel plate, respectively carry out 3 tension tests, using their mean value as characteristic value., as the intensity of the corresponding high strain rate of collision, utilize 10% stress of fluidity under strain rate 1000/s herein, and as the toughness under the corresponding low strain rate of compacting, measure the uniform elongation under strain rate 0.1/s.Using long-pending balanced index as intensity and toughness of these 10% stress of fluidity and uniform elongation.
Volume fraction V (%), 10% stress of fluidity in tension test under average crystal particle diameter D (μm), strain rate 1000/s, uniform elongation in the tension test under strain rate 0.1/s that the Cr carbide of these steel plates and Cr nitride are shown is concluded and the two is long-pending in table 2.
[table 2]
Steel plate 1 ~ 26 in table 2 is the steel plate of example of the present invention.Mo content in steel plate 1 ~ 26: 0.3%, Cu content: 0.3%, Ti, Nb, V content: 0.001% is the content as impurity.
Steel plate 1 ~ 26 all has excellent intensity and the harmony of toughness.Specifically, be 10% stress of fluidity under strain rate 1000/s and the long-pending steel more than 450MPa of the uniform elongation under strain rate 0.1/s.
On the other hand, steel plate 27 ~ 44 is comparative steel, is the steel of the harmony difference of intensity and toughness.
The C content of steel plate 27,28 is outside scope of the present invention, and therefore the harmony of intensity and toughness is poor.
The N content of steel plate 29,30 is outside scope of the present invention, and particularly (C+3 × N) amount of steel plate 29 is also less than scope of the present invention, and therefore the harmony of intensity and toughness is poor.
(C+3 × N) amount of steel plate 31,32 is less than scope of the present invention, and particularly the C content of steel plate 31 and N content are all outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Cr content of steel plate 33,34 and Md 30value is outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Ni content of steel plate 35 and Md 30value is outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Ni content of steel plate 36 and Md 30value is outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Si content of steel plate 37 and Mn content are outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Si content of steel plate 38, Mn content and Ti content are outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Mo content of steel plate 39 and Nb content are outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
The Cu content of steel plate 40 and V content are outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.
Steel plate 41,42 all has the chemical constitution, (C+3 × N) amount and the Md that meet scope of the present invention 30value, but crystal particle diameter is outside scope of the present invention, and therefore, the harmony of intensity and toughness is poor.By comparing the steel plate 1,41,42 made by steel grade A1, known, by crystal particle diameter is set to less than 10 μm, excellent intensity and the harmony of toughness can be obtained.
And then steel plate 43,44 all has the chemical constitution, (C+3 × N) amount and the Md that meet scope of the present invention 30value, but the cumulative volume rate of cold the Cr carbide and Cr nitride that prolong annealed material is more than 1%, and the harmony of intensity and toughness is poor.By comparing the steel plate 3,4,43,44 made by steel grade A3, known, by the cumulative volume rate of Cr carbide and Cr nitride is set to less than 1%, excellent intensity and the harmony of toughness can be obtained.
Fig. 2 is the figure of the analytical results that the hot-roll annealing plate utilizing EPMA X-ray analysis X is shown, (a) of Fig. 2 illustrates the analytical results of steel plate 3, (b) of Fig. 2 illustrates that the analytical results of steel plate 43, (c) of Fig. 2 illustrate the analytical results of steel plate 44.
Steel plate 43,44 is for meeting the chemical constitution of scope of the present invention, but annealing temperature and the annealing time of the hot-rolled sheet annealing after hot rolling do not meet (2) formula, from the EPMA analytical results of the hot-roll annealing plate of (c) of (a) ~ Fig. 2 of Fig. 2, after hot-rolled sheet annealing, there is the region of C, N multiviscosisty.They are residual until after final annealing, exist with the form of the carbide of a large amount of Cr, nitride.

Claims (5)

1. an austenite stainless steel plate, wherein, in mass %, C:0.02 ~ 0.30%, Cr:10.0 ~ 25.0%, Ni:3.5 ~ 10.0%, Si:0 ~ 3.0%, Mn:0.5% ~ 5.0%, N:0.10 ~ 0.40%, Mo:0 ~ 3.0%, Cu:0 ~ 3.0%, Ti:0 ~ 0.10%, Nb:0 ~ 0.50%, V:0 ~ 1.0%, C+3 × more than N:0.4%, surplus is made up of Fe and impurity, the Md specified by following (1) formula 30value is more than 0 DEG C and less than 50 DEG C, and the volume fraction of Cr carbide and Cr nitride is less than 1%, and the average crystal particle diameter of parent phase is less than 10 μm,
Md 30value (DEG C)=497-462 (%C+%N)-9.2 (%Si)-8.1 (%Mn)-13.7 (%Cr)-20 (%Ni+%Cu)-18.5 (%Mo) (1).
2. austenite stainless steel plate according to claim 1, wherein, in mass %, containing at least a kind in Si:0.1 ~ 3.0%, Mo:0.4 ~ 3.0%, Cu:0.4 ~ 3.0%.
3. according to austenite stainless steel plate according to claim 1 or claim 2, wherein, in mass %, one kind or two or more containing what be selected from the group that is made up of Ti:0.01 ~ 0.10%, Nb:0.02 ~ 0.50%, V:0.02 ~ 1.0%.
4. the austenite stainless steel plate according to any one in claims 1 to 3, wherein, amassing as more than 450MPa of 10% stress of fluidity under strain rate 1000/s and the uniform elongation under strain rate 0.1/s.
5. the manufacture method of an austenite stainless steel plate, hot rolling is implemented to stainless steel starting material, then with the annealing temperature T (DEG C) and annealing time t (sec) that meet following (2) formula, hot-rolled sheet annealing is implemented to gained hot-rolled steel sheet, described stainless steel starting material in mass %, C:0.02 ~ 0.30%, Cr:10.0 ~ 25.0%, Ni:3.5 ~ 10.0%, Si:0 ~ 3.0%, Mn:0.5% ~ 5.0%, N:0.10 ~ 0.40%, Mo:0 ~ 3.0%, Cu:0 ~ 3.0%, Ti:0 ~ 0.10%, Nb:0 ~ 0.50%, V:0 ~ 1.0%, C+3 × more than N:0.4%, surplus is made up of Fe and impurity,
t×exp(-25007/(T+273))＞9.36992×10 -6···(2)。
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