CN104250705B - Enamel steel with high-temperature baking hardenability and manufacturing method thereof - Google Patents

Enamel steel with high-temperature baking hardenability and manufacturing method thereof Download PDF

Info

Publication number
CN104250705B
CN104250705B CN201410483551.8A CN201410483551A CN104250705B CN 104250705 B CN104250705 B CN 104250705B CN 201410483551 A CN201410483551 A CN 201410483551A CN 104250705 B CN104250705 B CN 104250705B
Authority
CN
China
Prior art keywords
steel
enamel
indurative
temperature baking
temperature
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN201410483551.8A
Other languages
Chinese (zh)
Other versions
CN104250705A (en
Inventor
孙全社
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Baoshan Iron and Steel Co Ltd
Original Assignee
Baoshan Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Priority to CN201410483551.8A priority Critical patent/CN104250705B/en
Publication of CN104250705A publication Critical patent/CN104250705A/en
Priority to EP15841538.0A priority patent/EP3196328B1/en
Priority to PCT/CN2015/089695 priority patent/WO2016041490A1/en
Application granted granted Critical
Publication of CN104250705B publication Critical patent/CN104250705B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • 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
    • C21D8/0242—Flattening; Dressing; Flexing
    • 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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0442—Flattening; Dressing; Flexing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C21D2211/004—Dispersions; Precipitations

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention discloses enamel steel with high-temperature baking hardenability. The enamel steel comprises chemical elements in percentage by weight as follows: 0.008-0.020% of C, 0.05-0.50% of Mn, 0.021-0.035% of S, 0.005-0.050% of Alt or 0.003-0.045% of AlS, larger than 0 and less than 0.003% of N, larger than 0 and less than or equal to 0.010% of O and element Ti, wherein the weight percentage of element Ti meets the conditions N*Ti smaller than or equal to 3*10＜-4＞,S*Ti greater than or equal to 2*10＜-3＞ and Ti greater than or equal to 3.43N+1.5S+0.02, and the balance is Fe and unavoidable impurity elements. The invention further discloses a manufacturing method of the enamel steel, which comprises the steps of pretreatment of hot metal, converter smelting, refining, continuous casting and hot rolling. The enamel steel with high-temperature baking hardenability has relatively good forming property, good welding property, excellent firing property and excellent enameling property.

Description

One kind has the indurative Steel for enamel of high-temperature baking and its manufacture method
Technical field
The present invention relates to a kind of alloy steel products and its manufacture method, more particularly, to a kind of Steel for enamel and its manufacture method.
Background technology
For displacement type water heater, inner bag is its critical component, which determine water heater using safety and making Use the life-span.Have that corrosion resistance is good, case hardness is high with steel plate for the enamel inner container of bottom base, the smooth various features such as easy to clean, this The enamel inner container of sample has been significantly increased service life and the combination property of water heater liner.Heat is made for bottom base using steel plate During the enamel inner container of hydrophone, steel plate needs through blanking, shapes, welds laggard first, then carries out the application of slip, finally 830 DEG C about hot conditions under burn till.But, in order to meet the requirement producing high-quality enamel inner container, steel plate must is fulfilled for into Shape, intensity, weldability, scaling resistance, anti-pin hole and high temperature resistant many performance requirements such as burn till.
Before, enamel inner container is generally welded by three parts, i.e. two end caps and a ladle body, in therefore one enamel Courage typically has three road weld seams, it include twice circumferential weld with together with vertical masonry joint, the requirement to formability of two end caps is relatively low.So And, a kind of novel internal bladder occurs in prior art, this novel internal bladder is welded by upper barrel, lower barrel two parts, will be original Three road weld seams are reduced to middle one girth welding, and therefore, novel internal bladder eliminates edge rolling, reaming and twice in process Weld seam, manufacture craft is greatly simplified.Meanwhile, the minimizing of weld seam can be significantly increased the voltage endurance capability of inner bag.With When, because the punching press of novel internal bladder is deeper, after punching press, carry out the processing such as reaming again, thus, the punching performance to steel plate and reaming Performance requirement significantly improves.
In order to meet the processing request of inner bag, mainly adopt cold-rolled steel sheet, its forming property is better than hot rolled steel plate.Existing skill The steel plate being generally used for inner bag in art disclosure satisfy that punching press requires, but its reaming performance is relatively low, that is, reaming after deep-draw Easily ftracture.Simultaneously as lacking the suppression mechanism of ferrite crystal grain abnormal growth under high temperature, weld seam and heat after welding in steel The crystal grain severely subnormal of the zone of influence is grown up, and after high-temperature coating enamel firing becomes, crystal grain is also easily grown up, and causes steel plate mother metal, weld seam and heat The yield strength of the zone of influence etc. declines, and ultimately results in inner bag cracking leak easily around weld seam when suppressing.Further, since In steel, storage hydrogen trap is not enough, even if under the conditions of the one side application of slip of inner bag, also often produces the quick-fried phenomenon of squama.
Publication No. cn1966753a, publication date is on 2 23rd, 2007, a kind of entitled " hot-rolled double-side enamel steel The Chinese patent literature of plate and its manufacture method " is related to a kind of enamel sheet, and its each element composition (wt.%) is: c: 0.02%～0.06%, si :≤0.50%, mn:0.15%～0.40%, p :≤0.15%, s :≤0.006%, n≤ 0.003%, ti:0.08%～0.20%, als: 0.005%～0.055%, ti/c:2.2～5, balance of fe and inevitable Impurity.Hot-rolled state the following group is woven to the ferrite that crystal grain diameter is at 2 μm～20 μm, is uniform-distribution with diameter in the tissue and exists The tic particle of below 20nm.In technical scheme disclosed in this patent document, enamel sheet has the higher ti unit of content Element and the relatively low s element of content.
Publication No. cn101684532a, publication date is on March 31st, 2010, and entitled " a kind of cold rolling water heater is with warding off The Chinese patent literature of porcelain steel and production method " discloses a kind of glassed steel, and its chemical element weight/mass percentage composition is (wt.%) Composition composition: c:0.01%～0.08%, si≤0.03%, mn:0.10%～0.60%, p≤0.02%, s:0.003% ～0.02%, n:0.001%～0.006%, als≤ 0.04%, ti:0.02%～0.12%, remaining is iron and inevitable Impurity, the superfluous Ti content in steel meets relational expression: ti- (4*c+3.43*n+1.5s)≤0.This Chinese patent literature institute is public Yield strength after simulation enamel firing for the glassed steel opened is less than the yield strength before simulation enamel firing.
Publication No. cn101586210a, publication date be on November 25th, 2009, entitled " high strength enamel steel and its Produce and burning ward off technique " Chinese patent literature disclose a kind of be used for Steel for enamel, the percent mass of its each chemical element contains Measure and be: c:0.01～0.12, si≤0.03, mn:0.50～1.00, p≤0.070, s≤0.015, nb:0.020～0.050, Mo:0.05～0.30, als: 0.005～0.070, balance of fe and inevitable impurity.Meanwhile, this Steel for enamel also meets 10nb >=mo and 0.30≤10nb+mo≤0.50.
Content of the invention
It is an object of the invention to provide one kind has the indurative Steel for enamel of high-temperature baking, this Steel for enamel has excellent Good forming property, good welding performance and excellent application of slip performance.In addition, Steel for enamel of the present invention is also equipped with Excellent enamel firing performance, its yield strength after high temperature enamel firing can be obviously improved, that is, have high-temperature baking hardening.This Outward, the alloy of Steel for enamel of the present invention adds low cost.
To achieve these goals, the invention provides one kind has the indurative Steel for enamel of high-temperature baking, its chemistry Element percent mass proportioning is:
C:0.008～0.020%；
Mn:0.05～0.50%；
S:0.021～0.035%；
Alt 0.005～0.050% or als0.003～0.045wt.%；
0 ＜ n ＜ 0.003%；
0 ＜ o≤0.010%；
And ti element, and the weight/mass percentage composition of ti element meets n × ti≤3 × 10-4, s × ti >=2 × 10-3, ti ≥3.43n+1.5s+0.02；Balance of fe and inevitable impurity element.
In the technical program, inevitable impurity is primarily referred to as p element and si element.P content is easy in steel when higher In crystal boundary on segregation, thus, easily produce bubble and stain in enamel firing, thus affecting the surface quality of enamel.Si content The enamel property of steel not only can be damaged when higher, but also the very poor oxide of ductility can be formed and be mingled with, thus damaging steel Plasticity.For technical scheme, p element and si element are harmful elements, and their contents in steel need More low better, therefore, it can for the content of si element to be controlled to≤0.10wt.%, and the content of p element is controlled to≤ 0.035wt.%.
Of the present invention there is each chemical element in the indurative Steel for enamel of high-temperature baking design principle be:
C and ti: first, in steel, phosphorus content has a significant impact to the forming property of steel plate and intensity, and phosphorus content is higher, plasticity Lower, intensity is higher, and vice versa.Secondly, carbon, in steel in addition to solid solution presence, also can form cementite or pearlite etc. Microstructure.Additionally, after adding titanium alloy, carbon can also form carbonization titanium compound with titanium.
In the inventive solutions, by the content of control carbon content and the titanium elements reacting with carbon, and In conjunction with follow-up technology controlling and process so that carbon will not form pearlite microstructure, but with carbide (for example, the carbon in disperse Change titanium, cementite etc.) or a small amount of solution presence.Because in pearlite microstructure, cementite is assembled in a large number, on the one hand Substantial amounts of bubble can be formed during enamel, be on the other hand unfavorable for improving the intensity of steel during enamel firing.When carbon contains When amount is higher than 0.020wt.%, then carbon is readily formed more thick cementite, or even can produce pearlite microstructure, instead It, when carbon content is less than 0.008wt.%, and not only carburizing body burden is little in steel, and the titanium carbide being formed with titanium is also little, Invigoration effect, the intensity decreases of steel cannot be played, also do not reach the effect of high-temperature baking hardening.
For technical scheme, add the amount of titanium alloy particularly significant.Compound according to titanium is formed Solubility product calculates and understands: titanium first reacts with nitrogen, secondly reacts with sulphur, and last and carbon reacts, thus, with so Precipitation order, must ensure some titanium and carbon react after form titanium carbide.Quality when the titanium elements adding Percentage composition meets relational expression: it is possible to ensure some titanium and carbon reaction during ti >=3.43n+1.5s+0.02, and leads to Cross control hot rolling technology to make cementite particle little than existing cementite particle, and titanium carbide, titanium carbonitride are with tiny Graininess exists, to realize the purpose of matrix strengthening.Meanwhile, in enamel high temperature sintering process, originally with small and dispersed shape Cementite and titanium carbide, carbon titanium nitride particle that state exists, understand some dissolving during subsequent heat, and subsequent Separate out again in cooling procedure, the particle again separating out can more tiny, disperse, thus realize reach through pyroprocess The purpose of baking hardening.If on the contrary, the weight/mass percentage composition of titanium elements is too low, if the content being limited less than relational expression, I.e. during ti ＜ 3.43n+1.5s+0.02, then be difficult to guarantee in steel and there is a number of titanium carbide, titanium carbonitride particle, So, the purpose of precipitation strength cannot also be played.For this reason, it is impossible to further improve the strong of steel after burning till through high temperature Degree.Thus, should be controlled in the content with the c element in the indurative Steel for enamel of high-temperature baking of the present invention 0.008～0.020wt.%, and the content of ti element should meet: ti >=3.43n+1.5s+0.02.
In addition, it is further preferred that the content of c element is controlled between the scope of 0.015～0.020wt.%.
Mn: manganese is the deoxidant element in steel, adds it can control the content of oxygen in steel.Manganese can generate sulphur with reaction of Salmon-Saxl Change manganese.After adding titanium elements in steel, manganese also can form compound field trash, such as manganese sulfide titanium etc. therewith.This type impurity In spherical, the impact to processing characteristics for the manganese sulfide can be significantly decreased.However, when manganese content is too high, during enamel Steel and the reaction at enamel interface, the adherence of infringement enamel can be affected, and easily produce the defects such as bubble.In consideration of it, this The bright described mn content having in the indurative Steel for enamel of high-temperature baking is set as 0.05～0.50wt.%.
Preferably, there is the mn content in the indurative Steel for enamel of high-temperature baking further it is set as above-mentioned 0.1 ～0.3wt.%.
S: in general, the sulphur in steel is harmful element, this is because sulphur and manganese can form manganese sulfide inclusion thing, manganese sulfide Field trash can damage the horizontal plastic property of steel plate.However, s element not harmful element in the inventive solutions, need to control In Steel for enamel processed, s content is between 0.021～0.035wt.% scope, and also s × ti >=2 × 10 to be ensured-3.Why Sulfur content is controlled between 0.021～0.035wt.% scope, is because that, on the basis of adding titanium, sulphur and titanium can form sulphur Change titanium, substantial amounts of storage hydrogen trap can be formed around titanium sulfide particle, be not likely to produce the quick-fried defect of squama during enamel.Meanwhile, After adding titanium elements in steel, manganese sulfide formed in the steel adverse effect to steel plasticity can also be reduced.But, if sulphur Content is higher than 0.035wt.%, then sulphur needs to consume more titaniums and manganese to form sulfide, and the sulfide being formed Grain can be very big, so, can damage the plasticity of steel.In addition, the sulfide of larger particles is to the effect improving fish scaling resistance Extremely limited.Additionally, sulphur can form titanium sulfide with titanium or can form compound manganese sulfide titanium with titanium and manganese.By sulfur content Control and ensure s × ti >=2 × 10-3, so that titanium sulfide is formed prior to manganese sulfide.Its reason is the product of s × ti Bigger, then the formation temperature of titanium sulfide is higher, and titanium sulfide grain shape present spherical, so, in subsequent hot rolled process In can further improve the shape and size of titanium sulfide by controlling heating and milling step.Similarly, for manganese element For, manganese can also form compound manganese sulfide titanium inclusion with sulphur, titanium, and its grain shape is also rendered as spherical, for this reason, just keeping away Exempt to form simple plasticity manganese sulfide inclusion in steel, thus improving the processing characteristics of steel.
Additionally, s content in Steel for enamel is controlled to 0.021～0.03wt.% is a kind of technical scheme being more highly preferred to.
Alt or als: aluminium is also strong deoxidant element.Oxygen content in the steel when aluminium content is higher will reduce, conversely, working as When aluminium content is too low, then the oxygen content in steel will be lifted.Remain in the oxygen in steel and mainly form presence be mingled with oxide, It can seriously damage the plasticity of steel.Appropriate aluminium can reduce the oxygen content in steel, and thus, aluminium is necessarily to add in steel One of element.For this reason, for of the present invention there is the indurative Steel for enamel of high-temperature baking for, if al is (total with alt Aluminium) form limit, then need for alt content to be controlled to 0.005～0.050wt.%, if al is with alsThe form of (dissolved aluminum) Limit, then need to control alsFor 0.003～0.045wt.%.
N: nitrogen is one of inevitable relict element in steel.Generally nitrogen is solid solution element, after adding titanium in steel, due to Nitrogen easily forms metallic compound with titanium, and therefore, in the steel after adding titanium, nitrogen can more have precedence over sulphur and carbon, forms nitrogen with titanium Change titanium.Being formed of titanium nitride is successively relevant with the content of titanium, nitrogen, and this can calculate according to the solubility product that titanium nitride is formed, i.e. lg [ti] * [n]=5.4-15790/t, wherein, t is the solid solubility temperature of titanium nitride, and unit is k, ti and n is the quality hundred of element Divide content.Nitrogen and/or Ti content are higher, and the amount of the titanium nitride of formation is also higher, and particle is also bigger.Meanwhile, if desired fix The nitrogen of 0.001wt.%, then need to consume the titanium of 0.00343wt.%, the quality that titanium is consumed is about 3.43 times of the quality of nitrogen. Titanium nitride particles can form small hole, to be conducive to storage during enamel for the steel plate in machining deformation around particle Hydrogen, however, titanium nitride particles also can seriously damage other mechanical properties such as plasticity and the reaming performance of steel plate.Additionally, titanium nitride Intensity after enamel firing for the intensity and steel of particle nor raising steel.For this reason, in order to avoid forming thick nitridation in steel Titanium inclusion, and reduce the consumption to titanium for the nitrogen, nitrogen in steel is low as best one can, and Control of Nitrogen Content is 0 ＜ n ＜ 0.003wt.%, And meet n × ti≤3 × 10-4.
O: because molten steel mainly relies on reaction between carbon and oxygen in smelting process, therefore, oxygen is inevitable in steel.So And, the processing characteristics that oxide is mingled with and affects steel can be formed when oxygen content in steel is too high.Based on this, tool of the present invention There is the indurative Steel for enamel of high-temperature baking must be controlled to o: 0 ＜ o≤0.010wt.%.
In the inventive solutions, it is by following three constraint formulations for the restriction of the weight/mass percentage composition of titanium It is defined: 1) n × ti≤3 × 10-4, 2) and s × ti >=2 × 10-3, and 3) ti >=3.43n+1.5s+0.02.Namely Say, the constraint that the interpolation of ti element receives the weight/mass percentage composition of n and s element limits.
Because the phosphorus content in the Steel for enamel of the present invention is low, most of carbon can be fixed to form carbonization in steel plus after titanium Titanium compound, this makes carbon under free state or carburizing body burden is all few, and this can press down during the application of slip significantly The generation of needle pore defect processed, thus be significantly increased the service life of enamel inner container.
Further, the c element having in the indurative Steel for enamel of high-temperature baking of the present invention is with the carbon of disperse Compound form exists.
Further, described carbide is cementite and the tiny titanium carbide of particle, titanium carbonitride.
Further, described titanium carbide, the particle diameter of carbon titanium nitride particle are 10～30 μm.
Further, have in the indurative Steel for enamel of high-temperature baking of the present invention, also contain 0 ＜ cu≤ 0.10%th, 0 ＜ cr≤0.10%, 0 ＜ ni≤0.10%, 0 ＜ mo≤0.10%, 0 ＜ nb≤0.010%, 0 ＜ v≤ 0.020%th, at least one of 0 ＜ b≤0.0005%, and 0.05%≤5 × nb+cu+v+ni+cr+mo+10 × b≤ 0.20%.
The content fluctuation of the copper in steel, chromium, nickel and molybdenum all can affect the enamel property of steel plate, particularly can affect steel Adherence, and surface defect can be produced, also can affect intensity and the plasticity of steel plate.In order to be further ensured that the application of slip of steel Can etc. reliable and stable, these addition element are controlled to: 0 ＜ cu≤0.10wt.%, 0 ＜ cr≤0.10wt.%, 0 ＜ ni≤ 0.10wt.%, 0 ＜ mo≤0.10wt.%
Add the recrystallization temperature that niobium, vanadium and boron can improve steel.Once recrystallization temperature improves, then the heat of steel plate Roll temperature to be also required to correspondingly improve.For thin specification steel plate, for example, finished product thickness is in the steel plate of below 2.5mm, too high end It is difficult to realize for rolling temperature, and can cause the problem of the temperature inequality of steel band different parts, ultimately results in the mixed crystal of steel plate With tissue abnormalities defect.In addition, though the raising of recrystallization temperature has certain effect for the intensity improving before enamel sintering, But for the intensity not too big effect improving after enamel sintering.In order to reduce these addition element to micro- after hot rolling Tissue adverse effect, need by they control within limits, that is, 0 ＜ nb≤0.010wt.%, 0 ＜ v≤ 0.020wt.%, 0 ＜ b≤0.0005wt.%.
Meanwhile, above-mentioned element also needs to when adding meet: 0.05wt.%≤5 × nb+cu+v+ni+cr+mo+10 × B≤0.20wt.%.
Correspondingly, present invention also offers a kind of production mentioned above has the indurative Steel for enamel of high-temperature baking Manufacture method, this manufacture method includes step: molten iron pretreatment → converter smelting → refining → continuous casting → hot rolling.
Further, the hot rolling in the manufacture method with the indurative Steel for enamel of high-temperature baking of the present invention walks Also include successively after rapid: pickling → cold rolling → annealing → smooth.
Further, in described cold rolling step, total reduction is controlled to be more than 70%.It is further preferred that controlling cold rolling Total reduction >=75%.In addition, surface of steel plate can also be controlled thick by changing the roughness of roll surface in cold rolling step Rugosity is in 0.4～2.0 μ m.
Further, in described annealing steps, annealing temperature is 650-800 DEG C.
Further, in above-mentioned hot-rolled step, heating-up temperature is 1100～1250 DEG C, the heat time >=thickness of slab × 1min/mm, wherein thickness of slab unit are mm, and wherein this thickness of slab refers to continuous casting billet thickness of slab.
In order to ensure that the microstructure in steel forms uniform austenite, i.e. abundant austenitizing, and make in steel billet The cementite assembled or pearlite dissolving, that is, make the dissolvings such as the particle such as titanium nitride of some high temperature formation or be partly dissolved, will The heating-up temperature of continuous casting billet is set as 1100～1250 DEG C.Certainly, the concrete heat time within the range can be according to steel billet Thickness is adjusted, and general steel billet is thinner, and its heat time is shorter, and its heat time needs to meet t >=thickness of slab × 1min/ mm.
Further, in above-mentioned hot-rolled step, hot rolling finishing temperature is 850～930 DEG C, and hot-rolling coiling temperature is 630～780 DEG C.
Because, in hot-rolled step, in casting process, carbide of dissolving etc. can be analysed in the form of compound again before Go out, accordingly, it would be desirable to reasonably control the finishing temperature in hot-rolled step, so that carbide assumes small and dispersed state and is distributed in In ferritic matrix.In consideration of it, controlling the Steel for enamel of the present invention to complete hot rolling finish to gauge in 850～930 DEG C of temperature ranges, To guarantee that hot rolling completes more than recrystallization temperature, it is to avoid in austenite+ferrite two-phase section rolling, prevent from causing steel plate mixed crystal Defect with tissue abnormalities.
The manufacture method with the indurative Steel for enamel of high-temperature baking of the present invention is passed through to control in hot-rolled step Technological parameter come to make cementite and titanium carbide with fine particle state exist, to reach the purpose of matrix strengthening.Additionally, passing through The finishing temperature in heating-up temperature and hot-rolled step in continuous casting step and coiling temperature is controlled further to improve sulfuration in steel The shape and size of titanium.
Compared to existing Steel for enamel, of the present invention have the indurative Steel for enamel of high-temperature baking through high temperature Yield strength after enamel firing is obviously improved, thus improve the voltage endurance capability of Steel for enamel product, extends its service life.
Of the present invention have the indurative Steel for enamel of high-temperature baking and possess preferable processability, and its elongation percentage >= 39%, hole expansibility >=60%, it is particularly suitable for making the water heater liner of various complicated shapes.
Of the present invention have the indurative Steel for enamel of high-temperature baking and possess good welding performance.
Of the present invention have the indurative Steel for enamel of high-temperature baking and possess excellent application of slip performance, when its hydrogen penetrates Between long (>=10min), higher than the hydrogen permeation time (>=8min) of counterenamel steel in prior art.
The alloy addition element relatively low due to employing price, of the present invention have the indurative enamel of high-temperature baking Cost of alloy with steel is low, manufacturing cost also relatively economical.
The simple production process of the manufacture method with the indurative Steel for enamel of high-temperature baking of the present invention is easy.
Brief description
Fig. 1 has the indurative Steel for enamel of high-temperature baking under 830 DEG C of keeping warm modes with insulation for embodiment a1 The tendency chart of the yield strength of time passage.
Fig. 2 is the micro-organization chart with the indurative Steel for enamel of high-temperature baking of embodiment a1.
Fig. 3 is the shape appearance figure of the precipitated phase having in the indurative Steel for enamel of high-temperature baking of embodiment a1.
Specific embodiment
The indurative Steel for enamel of high-temperature baking and its system will be had to of the present invention according to specific embodiment below The method of making is made and being further illustrated, but specific embodiment and related description are not constituted for technical scheme not Work as restriction.
Embodiment a1-a6 and comparative example b1
(1)-(5) manufacture the Steel for enamel in embodiment a1-a5 and comparative example b1 as steps described below, according to following steps Suddenly the Steel for enamel in (1)-(9) manufacture embodiment a6:
1) molten iron pretreatment；
2) converter smelting: decarburization, dephosphorization are realized by top and bottom combined blown converter, removes residual elements and pernicious gas etc.；
3) refine: further slough pernicious gas and residual elements, add the alloying elements such as titanium, in enter the deoxidations such as aluminium, Realize being precisely controlled of chemical composition.Control the percent mass proportioning of each chemical element of embodiment a1-a6 and comparative example b1 such as Shown in table 1；
4) continuous casting: molten steel is cast into the thick continuous casting billet of 200,230mm, after continuous casting billet cooling, Surface Quality is carried out manually Check, labor cleaning is carried out to surface defect；
5) hot rolling: before hot rolling, continuous casting billet is heated, heating-up temperature is 1100～1250 DEG C, heat time t >=thickness of slab × 1min/mm, wherein thickness of slab unit are mm；The continuous casting billet thick to 200mm, its heat time controls in 200～240min or more Long, to the continuous casting billet that 230mm is thick, its heat time controls in 230～260min or longer；As needed, hot rolling end of a period thickness For 1.5～18mm, hot rolling finishing temperature is 850～930 DEG C, is batched, hot rolled coil after section cooling to coiling temperature Temperature is taken to be 630～780 DEG C；
6) pickling: the main hydrochloric acid using dilution carries out pickling it is also possible to take alternate manner to carry out pickling, the mesh of pickling Be the iron scale eliminating surface；
7) cold rolling: to control total reduction more than 70%；
8) anneal: anneal at 650～800 DEG C it is therefore an objective to realize the recrystallization of cold rolling rear steel plate tissue and crystal grain is grown up, with Obtain good plasticity；
9) smooth: smooth elongation percentage is 0.8～1.2%.
In each step, specific process parameter is referring particularly to table 2.
Table 1 lists the quality hundred of each chemical element in this case embodiment a1-a6 and the Steel for enamel of comparative example b1 Distribution ratio.
Table 1. (wt.%, balance of fe and other the inevitable impurity in addition to p and si)
Sequence number a1 a2 a3 a4 a5 a6 b1
c 0.013 0.018 0.02 0.008 0.01 0.013 0.031
mn 0.25 0.2 0.1 0.3 0.25 0.15 0.22
s 0.029 0.025 0.035 0.025 0.03 0.021 0.007
al 0.041 0.035 0.035 0.028 0.005 0.02 0.031
n 0.0018 0.002 0.0025 0.0015 0.002 0.002 0.0026
o 0.005 0.006 0.003 0.005 0.003 0.003 --
p 0.011 0.015 0.009 0.01 0.008 0.011 0.01
si 0.008 0.02 0.05 0.03 0.1 0.008 0.006
ti 0.09 0.08 0.09 0.085 0.15 0.12 0.002
cu 0.01 0.02 0.02 0.05 0.01 0.06 --
cr 0.02 0.05 0.02 0.015 0.05 0.06 --
ni 0.008 0.025 0.008 0.01 0.02 0.005 --
mo 0.005 0.005 0.015 0.008 0.02 0.01 --
nb 0.005 0.002 0.002 -- -- 0.002 --
v 0.015 -- -- -- 0.005 0.01 --
b -- 0.0002 -- -- 0.0004 -- --
Relational expression 1) 0.00016 0.00016 0.00023 0.00013 0.0003 0.00024 5.2×10-6
Relational expression 2) 0.0026 0.002 0.0032 0.0021 0.0045 0.0025 1.4×10 -5
Relational expression 3) 0.07 0.064 0.081 0.063 0.072 0.058 0.039
Relational expression 4) 0.02 0.016 0.009 0.022 0.078 0.062 -0.037
Relational expression 5) 0.08 0.11 0.07 0.08 0.11 0.16 0
Note: relational expression 1) n × ti, relational expression 2) s × ti, relational expression 3) 3.43n+1.5s+0.02, relational expression 4) ti- (3.43 × n+1.5 × s+0.02), relational expression 5) 5 × nb+cu+v+ni+cr+mo+10 × b.
Table 2 lists the technological parameter of the manufacture method of the Steel for enamel of this case embodiment a1-a6 and comparative example b1.
Table 2.
At room temperature, embodiment a1-a6 and comparative example b1 are all sampled using horizontal, measure rel、rm、a80mmAnd reaming Rate.The hydrogen storage capacity weighing the Steel for enamel of embodiment a1-a6 and comparative example b1 is then according to the electrochemistry in standard en10209 Experimental technique is measuring the hydrogen permeation time of steel plate, and is all converted into the standard thickness of 1mm.
Under 830 DEG C of keeping warm mode, embodiment a1-a6 and comparative example b1 are all carried out at heat using after horizontal sampling Reason, that is, take out after being placed on 830 DEG C of constant temperature oven inside holding 10min and be air cooled to room temperature.Model after Overheating Treatment, measures rel、rmAnd a80mm.
The Steel for enamel that table 3 lists in this case embodiment a1-a6 and comparative example b1 is distinguished at room temperature with 830 DEG C Mechanical property parameters under keeping warm mode.
Table 3.
From table 3 it is observed that at room temperature, the yield strength of embodiment a1-a6 all >=197mpa, tensile strength all >= 315mpa, elongation percentage a80>=39%, hole expansibility >=70%, hydrogen permeation time >=12min, and under 830 DEG C of keeping warm modes, real The yield strength applying an a1-a6 has brought up to >=315mpa, tensile strength all >=412mpa, elongation percentage a80>=40%, thus may be used To illustrate, the Steel for enamel of the present invention not only has higher elongation percentage, a longer hydrogen permeation time, higher hole expansibility, and And yield strength after in 830 DEG C of insulation 10min of all embodiments and tensile strength all obtain and are significantly increased, this Illustrate that the glassed steel that the technical program is related to has excellent high-temperature baking hardening, have this to be beneficial to enamel use is significantly increased The voltage endurance capability of steel part and service life.
Hydrogen permeation time >=the 12min of Steel for enamel of the present invention.As a rule, as hydrogen permeation time >=8min When, steel plate just can meet anti-squama during counterenamel is quick-fried to be required that is to say, that no matter adopted which kind of type glaze in actual production Material, such steel plate can meet the quick-fried requirement of anti-squama.Because counterenamel is more more severe than the quick-fried performance requirement of one side enamel antagonism squama Carve, therefore, the Steel for enamel of the present invention is fully able to meet the requirement of one side enamel.
Fig. 1 show embodiment a1 have the indurative Steel for enamel of high-temperature baking under 830 DEG C of keeping warm modes with The trend of the yield strength of time passage.
As shown in figure 1, under 830 DEG C of keeping warm modes, the Steel for enamel of embodiment a1 is when not yet reaching the insulation of regulation Between (about 10min) when, the yield strength of the Steel for enamel of embodiment a1 increases with the passage of temperature retention time, but is reaching After the temperature retention time of regulation, its yield strength reduces with the passage of temperature retention time.But, even if in 830 DEG C of keeping warm modes Under temperature retention time long again, its yield strength still has raising by a relatively large margin compared to its yield strength under room temperature situation.
Fig. 2 shows the microstructure of the Steel for enamel of embodiment a1, and Fig. 3 then shows the precipitation in this Steel for enamel The shape appearance figure of phase.
As shown in Figures 2 and 3, the microstructure of the Steel for enamel of embodiment a1 is uniform ferritic structure, there are no Pearlitic structrure and the cementite particle of large-size, its precipitated phase is in tiny, Dispersed precipitate, with titanium carbide or titanium carbonitride is Main.
It should be noted that listed above is only the specific embodiment of the present invention it is clear that the invention is not restricted to above reality Apply example, have the similar change of many therewith.If those skilled in the art directly derive from present disclosure or The all deformation associated, all should belong to protection scope of the present invention.

Claims (11)

1. one kind has the indurative Steel for enamel of high-temperature baking, and its chemical elements in percentage by mass is: c:0.008～ 0.020%th, mn:0.05～0.50%, s:0.021～0.035%, alt:0.005～0.050% or als: 0.003～ 0.045%th, 0 ＜ n ＜ 0.003%, 0 ＜ o≤0.010% and ti element, and the weight/mass percentage composition of ti element meets n × ti ≤3×10-4, s × ti >=2 × 10-3, ti >=3.43n+1.5s+0.02, balance of fe and inevitable impurity element；
Wherein, described c element is existed with the carbide form of disperse, and described carbide is cementite and the tiny carbonization of particle Titanium, titanium carbonitride, described titanium carbide, the particle diameter of carbon titanium nitride particle are 10～30 μm.
2. there is high-temperature baking indurative Steel for enamel as claimed in claim 1 it is characterised in that also contain 0 ＜ cu≤ 0.10%th, 0 ＜ cr≤0.10%, 0 ＜ ni≤0.10%, 0 ＜ mo≤0.10%, 0 ＜ nb≤0.010%, 0 ＜ v≤ 0.020%th, at least one of 0 ＜ b≤0.0005%, and 0.05%≤5 × nb+cu+v+ni+cr+mo+10 × b≤ 0.20%.
3. there is high-temperature baking indurative Steel for enamel as claimed in claim 1 it is characterised in that described c constituent content For c:0.015～0.020%.
4. there is high-temperature baking indurative Steel for enamel as claimed in claim 1 it is characterised in that described s constituent content For 0.021～0.030%.
5. there is high-temperature baking indurative Steel for enamel as claimed in claim 1 it is characterised in that described mn constituent content For 0.1～0.3%.
6. the manufacture method with the indurative Steel for enamel of high-temperature baking as described in any one in Claims 1 to 5, its It is characterised by, including step: molten iron pretreatment → converter smelting → refining → continuous casting → hot rolling.
7. there is the manufacture method of the indurative Steel for enamel of high-temperature baking as claimed in claim 6 it is characterised in that in institute After stating hot-rolled step, also include successively: pickling → cold rolling → annealing → smooth.
8. there is the manufacture method of the indurative Steel for enamel of high-temperature baking as claimed in claim 7 it is characterised in that in institute State in cold rolling step, control total reduction to be more than 70%.
9. there is the manufacture method of the indurative Steel for enamel of high-temperature baking as claimed in claim 7 it is characterised in that in institute State in annealing steps, annealing temperature is 650-800 DEG C.
10. there is the manufacture method of the indurative Steel for enamel of high-temperature baking as claimed in claim 6 it is characterised in that In described hot-rolled step, heating-up temperature is 1100-1250 DEG C, and the heat time >=thickness of slab × 1min/mm, wherein thickness of slab unit is mm.
11. manufacture methods as claimed in claim 6 with the indurative Steel for enamel of high-temperature baking it is characterised in that In described hot-rolled step, hot rolling finishing temperature is 850-930 DEG C, and hot-rolling coiling temperature is 630-780 DEG C.
CN201410483551.8A 2014-09-19 2014-09-19 Enamel steel with high-temperature baking hardenability and manufacturing method thereof Active CN104250705B (en)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN201410483551.8A CN104250705B (en) 2014-09-19 2014-09-19 Enamel steel with high-temperature baking hardenability and manufacturing method thereof
EP15841538.0A EP3196328B1 (en) 2014-09-19 2015-09-16 Enamel steel having high-temperature baking hardenability and manufacturing method therefor
PCT/CN2015/089695 WO2016041490A1 (en) 2014-09-19 2015-09-16 Enamel steel having high-temperature baking hardenability and manufacturing method therefor

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201410483551.8A CN104250705B (en) 2014-09-19 2014-09-19 Enamel steel with high-temperature baking hardenability and manufacturing method thereof

Publications (2)

Publication Number Publication Date
CN104250705A CN104250705A (en) 2014-12-31
CN104250705B true CN104250705B (en) 2017-01-18

Family

ID=52185951

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201410483551.8A Active CN104250705B (en) 2014-09-19 2014-09-19 Enamel steel with high-temperature baking hardenability and manufacturing method thereof

Country Status (3)

Country Link
EP (1) EP3196328B1 (en)
CN (1) CN104250705B (en)
WO (1) WO2016041490A1 (en)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104250705B (en) * 2014-09-19 2017-01-18 宝山钢铁股份有限公司 Enamel steel with high-temperature baking hardenability and manufacturing method thereof
CN104928577B (en) * 2015-06-18 2017-08-25 宝山钢铁股份有限公司 A kind of steel plate and its manufacture method with high hole expansibility and excellent application of slip performance
CN107419183A (en) * 2016-05-23 2017-12-01 上海梅山钢铁股份有限公司 A kind of two-period form enamel internal container of water-heater hot rolled steel plate and its manufacture method
CN106222551B (en) * 2016-08-16 2018-05-01 武汉钢铁有限公司 A kind of flawless nitriding iron ware substrate in surface and production method
CN108796391B (en) * 2017-04-26 2020-12-22 宝山钢铁股份有限公司 Glass-lined steel with excellent plasticity and toughness and fish scaling resistance and manufacturing method thereof
CN107574375B (en) * 2017-08-31 2019-06-07 武汉钢铁有限公司 Counterenamel hot rolling acid-cleaning steel plate and its manufacturing method with excellent application of slip performance
CN109554607A (en) * 2017-09-25 2019-04-02 上海梅山钢铁股份有限公司 Cold rolling enamelled pressed steel and its manufacturing method with excellent scaling resistance and deep drawing quality
CN110777301B (en) * 2018-07-30 2021-05-14 宝山钢铁股份有限公司 Cold-rolled enamel steel and manufacturing method thereof
CN109652739B (en) * 2019-01-22 2020-08-18 山东钢铁股份有限公司 High-strength cold-rolled steel strip for enamel and preparation method thereof
CN109943779B (en) * 2019-04-30 2021-02-05 马鞍山钢铁股份有限公司 Low-carbon cold-rolled steel plate for enamel and production method thereof
KR102405223B1 (en) * 2020-11-05 2022-06-02 주식회사 포스코 Steel sheet for enamel and method of manufacturing the same
CN112941418B (en) * 2021-02-07 2022-08-05 首钢集团有限公司 High-strength steel for cold rolling enamel and preparation method thereof
CN114395688A (en) * 2021-12-09 2022-04-26 安阳钢铁集团有限责任公司 Production process of low-carbon enamel steel

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58197254A (en) * 1982-05-11 1983-11-16 Nippon Steel Corp Steel plate for enamel with superior secondary workability and deep drawability
KR970011629B1 (en) * 1994-12-20 1997-07-12 김만제 Method of manufacturing cold rolling sheet
KR100347570B1 (en) * 1997-08-29 2002-09-18 주식회사 포스코 Method for manufacturing steel sheet for enameled ironware with excellent formability and surface property
KR100360095B1 (en) * 1998-08-28 2003-10-22 주식회사 포스코 Manufacturing method of high adhesion enameled steel sheet with excellent formability
JP4102115B2 (en) * 2002-06-12 2008-06-18 新日本製鐵株式会社 Steel plate for enamel excellent in workability, aging property and enamel characteristics and method for producing the same
PT1950317E (en) * 2005-11-09 2016-06-03 Shin Nippon Seitetsu Kk (Nippon Steel Corporation) Steel sheet for continuous cast enameling with excellent resistance to fishscaling and process for producing the same
CN100453678C (en) * 2005-11-16 2009-01-21 鞍钢股份有限公司 Steel plate for hot-rolled double-side enamel and method for producing same
CN100473742C (en) * 2006-04-29 2009-04-01 宝山钢铁股份有限公司 Hot-rolled fine-grained steel for electrostatic enamel and manufacturing method thereof
CN101684532A (en) * 2008-09-27 2010-03-31 鞍钢股份有限公司 Enamel steel for cold rolling water heater and manufacturing method thereof
CN102251192A (en) * 2010-05-19 2011-11-23 宝山钢铁股份有限公司 Enamel steel and production method thereof
CN102433501B (en) * 2011-12-02 2013-08-28 山西太钢不锈钢股份有限公司 High strength and toughness strip steel and manufacturing method thereof
CN102747309A (en) * 2012-07-27 2012-10-24 宝山钢铁股份有限公司 Steel for enamel and production method thereof
CN103540845B (en) * 2013-11-07 2016-01-20 武汉钢铁(集团)公司 Yield strength is latten Glassed Steel and the manufacture method of 330MPa level
CN103741026A (en) * 2013-12-26 2014-04-23 马钢(集团)控股有限公司 240MPa-level hot-rolled pickled steel plate for single-sided enameling and production method of 240MPa-level hot-rolled pickled steel plate
CN104250705B (en) * 2014-09-19 2017-01-18 宝山钢铁股份有限公司 Enamel steel with high-temperature baking hardenability and manufacturing method thereof

Also Published As

Publication number Publication date
EP3196328B1 (en) 2019-08-14
WO2016041490A1 (en) 2016-03-24
EP3196328A1 (en) 2017-07-26
CN104250705A (en) 2014-12-31
EP3196328A4 (en) 2018-04-18

Similar Documents

Publication Publication Date Title
CN104250705B (en) Enamel steel with high-temperature baking hardenability and manufacturing method thereof
CN107208212B (en) Thick-walled high-toughness high-strength steel plate and method for producing same
CN104120368B (en) A kind of automobile frame high intensity austenitic stainless steel and its manufacturing method
JP6229640B2 (en) Seamless steel pipe and manufacturing method thereof
JP4650006B2 (en) High carbon hot-rolled steel sheet excellent in ductility and stretch flangeability and method for producing the same
CN109097680B (en) Method for manufacturing high-manganese high-aluminum nonmagnetic steel plate smelted by 50t intermediate frequency induction furnace
JP2016510361A (en) 780 MPa class cold rolled duplex steel and method for producing the same
CN104342601B (en) Ti-containing low-manganese and low-silicon hot-rolled steel with Rel being greater than or equal to 400MPa and production method adopting CSP (cast steel plate)
CN104131238B (en) High molding high durable Ultra-thin hot rolled steel plate and CSP production technology thereof
CN110129673A (en) A kind of 800MPa grades of high strength and ductility Q&P steel plate and preparation method thereof
CN108342654A (en) The manufacturing method of the cold rolling glassed steel of yield strength 230MPa or more
CN103667948A (en) Multiphase steel and preparation method thereof
CN110747405B (en) One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof
JP6056235B2 (en) Method for producing high-tensile steel sheet with excellent weldability and delayed fracture resistance and tensile strength of 950 MPa or more
JP5747249B2 (en) High-strength steel material excellent in strength, ductility and energy absorption capacity and its manufacturing method
JP2001115233A (en) High strength steel sheet excellent in weldability and stress corrosion cracking resistance and producing method therefor
CN108588559A (en) The cold rolling glassed steel of yield strength 230MPa or more
CN104928577B (en) A kind of steel plate and its manufacture method with high hole expansibility and excellent application of slip performance
JP6056236B2 (en) Method for producing high-tensile steel sheet having excellent weldability and delayed fracture resistance and tensile strength of 780 MPa or more
CN110273106B (en) 260 MPa-grade cold-rolled continuous-annealing enamel steel and production method thereof
JPH06184636A (en) Production of high strength and high toughness seamless steel pipe excellent in weldability
JP6051735B2 (en) Method for producing high-tensile steel sheet with excellent weldability and delayed fracture resistance
CN110066966A (en) A kind of low internal stress titaniferous high-strength steel and production method
CN110863136A (en) High-hole-expansion-performance hot rolled steel plate for enamel liner of water heater and manufacturing method thereof
CN108396235A (en) A kind of enamel matrix hot rolling steel plate and its manufacturing method

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C14 Grant of patent or utility model
GR01 Patent grant