EP2770076A1 - Rostfreier duplexstahl, platte aus dem rostfreien duplexstahl und material aus dem rostfreien duplexstahl - Google Patents

Rostfreier duplexstahl, platte aus dem rostfreien duplexstahl und material aus dem rostfreien duplexstahl Download PDF

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Publication number
EP2770076A1
EP2770076A1 EP12842430.6A EP12842430A EP2770076A1 EP 2770076 A1 EP2770076 A1 EP 2770076A1 EP 12842430 A EP12842430 A EP 12842430A EP 2770076 A1 EP2770076 A1 EP 2770076A1
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Prior art keywords
stainless steel
duplex stainless
less
amount
steel
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EP12842430.6A
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English (en)
French (fr)
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EP2770076A4 (de
EP2770076B1 (de
Inventor
Shinji Tsuge
Yuusuke Oikawa
Hiroshi Urashima
Haruhiko Kajimura
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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Priority claimed from JP2011231352A external-priority patent/JP5329632B2/ja
Priority claimed from JP2011266351A external-priority patent/JP5329634B2/ja
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • a general-purpose duplex stainless steel contains a large amount of Cr, Mo, Ni, and N and has favorable corrosion resistance.
  • Mo and Ni which are expensive, the alloy cost is high and the manufacturability is not favorable.
  • the price of steel material is not cheap and the duplex stainless steel is not widely used in place of 316 grade stainless steel or 317 grade stainless steel.
  • the present invention finds a measure for solving the problems described above by clarifying the relationship between the amount of Sn and hot manufacturability in an alloy-saving type duplex stainless steel.
  • the present invention finds a measure for solving the problems described above by clarifying the relationship between the amounts of Sn and Cu and hot manufacturability in a general-purpose duplex stainless steel. Due to this, the object of the present invention is to provide an Sn-containing duplex stainless steel, a cast steel of a duplex stainless steel, and a duplex stainless steel material which are inexpensive and have favorable hot manufacturability.
  • Such a duplex stainless steel is expected to have an excellent balance between corrosion resistance and cost. For this reason, it is considered that the possibility that the duplex stainless steel will be widely used in various fields is high.
  • an object of a second aspect (a second embodiment) of the invention is to develop an inexpensive general-purpose duplex stainless steel where the amounts of Ni and Mo, which are expensive elements, are reduced by increasing the amounts ofN and Mn and adding a combination of Cu and Sn.
  • the present inventors observed an edge cracking length which was generated when a cast steel of an alloy-saving type Sn-containing duplex stainless steel, which was obtained by vacuum melting and casting, was subjected to hot rolling. As a result, it was found that there rarely exists a cast steel of an Sn-containing duplex stainless steel in which a number of edge cracks is small.
  • Hot rolling experiments were performed as follows. First, a cast steel with a thickness of 90 to 44 mm was heated to 1200°C. Next, the thickness of the cast steel was reduced to a thickness of 12 to 6 mm by a plurality of rolling passes. The finishing rolling temperature was controlled to be approximately 900°C.
  • the present inventors observed an edge cracking length which was generated when a cast steel of a general-purpose duplex stainless steel, which was obtained by vacuum melting and casting, was subjected to hot rolling. As a result, it was discovered that there rarely exists an Sn-containing duplex stainless steel material in which a number of edge cracks is small.
  • Hot rolling experiments were performed as follows. First, a cast steel with a thickness of 90 to 44 mm was heated to 1200°C. Next, the thickness of the cast steel was reduced to a thickness of 12 to 6 mm by a plurality of rolling passes. The finishing rolling temperature was controlled to be approximately 900°C. Edge cracking was generated on the left and right sides and the maximum lengths on both sides were totaled to obtain the edge cracking length.
  • the amount of Cr is set to be in a range of 18.0% or more and 25.0% or less.
  • the amount of Cr is preferably in a range of 19.0% to 23.0%.
  • Sn is contained in order to improve the corrosion resistance of the steel of the present embodiment. For this reason, it is necessary that at least 0.01% of Sn be contained. Furthermore, it is preferable that 0.02% or more of Sn be contained.
  • Sn is an element which inhibits the hot manufacturability of the steel, and decreases the hot strength of the interface between the ferrite phase and the austenite phase, particularly at a temperature of 900°C or less in the alloy element saving type duplex stainless steel which is the subject of the present embodiment. The degree of the decrease depends on the amounts of S, Ca, and O; however, when more than 0.2% of Sn is contained, it is not possible to prevent the decrease in the hot manufacturability even by restricting other limits in the present embodiment. Therefore, the upper limit of the amount of Sn is set to 0.2%.
  • the pitting resistance is impaired.
  • the upper limit of Ca/O is set to be in a range of 1.0.
  • Ca/O is preferably in a range of 0.4 to 0.8.
  • the cast steel of the stainless steel indicates a steel in a state after casting and before processing such as hot working, forging, or the like is performed
  • the stainless steel material indicates a semi-finished product, a hot-rolled steel plate, a cold-rolled steel plate, a steel wire, a steel pipe, or the like after processing the cast steel by various methods.
  • the stainless steel indicates the general forms for a steel such as a cast steel, a steel material, and the like.
  • the processing described above includes hot and cold processings.
  • P is an element which is inevitably mixed in from raw materials and the amount of P is limited to be in a range of 0.05% or less since P degrades the hot workability and the toughness.
  • the amount of P is preferably in a range of 0.03% or less.
  • the amount of Cr is set to be in a range of 23.0% or more to 28.0% or less.
  • the amount of Cr is preferably in a range of 24.0% to 27.5%.
  • Ni stabilizes the austenitic structure and improves the toughness and the corrosion resistance with respect to various types of acid. Furthermore, Ni suppresses a decrease in hot workability due to the addition of Sn and Cu. For this reason, 2.0% or more of Ni is contained. By increasing the amount of Ni, it is possible to decrease the nitride precipitation temperature. On the other hand, since Ni is an expensive alloy, the amount of Ni is limited to be in a range of 6.0% or less. The amount of Ni is preferably in a range of 2.5% to 5.5%, and more preferably in a range of 3.0% to 5.0%.
  • Non-Patent Document 1 Ni increases the solid solubility of Cu and has an effect of suppressing the generation of a liquid phase having a low melting point due to the addition of Cu and Sn.
  • Co is an element which belongs to the same group as Ni. For this reason, it is considered that the decrease in the hot workability due to Cu and Sn is suppressed by increasing the sum of the amounts of Ni and Co.
  • Ca is an important element for the hot manufacturability of the steel, and it is necessary that Ca be contained in order to fix the S and O in the steel as inclusions and to improve the hot manufacturability.
  • 0.0010% or more of Ca is contained for this purpose.
  • addition of an excessive amount thereof decreases the pitting resistance. For this reason, the upper limit of the amount of Ca was set to 0.0040%.
  • O is an inevitable impurity and an upper limit thereof is not particularly set; however, O is an important element which configures oxides which are representatives of non-metallic inclusions. Composition control of the oxides is extremely important for the improvement of the hot manufacturability. In addition, surface defects are caused when coarse cluster-shaped oxides are generated. For this reason, it is necessary to limit the amount of O so as to be low.
  • the upper limit of the amount of O is preferably in a range of 0.005% or less.
  • Mo is an element which is extremely effective at incrementally increasing the corrosion resistance of the stainless steel, and Mo can be contained according to necessity. In order to improve the corrosion resistance, it is preferable that 0.2% or more of Mo be contained. On the other hand, Mo is an expensive element, and from the point of view of suppressing the cost of the alloy in the steel of the present embodiment, the upper limit of the amount of Mo is set to 2.0%.
  • Nitrides and carbides which are formed of Nb are generated in the hot working and the cooling process of the steel material, and these have the effect of increasing the corrosion resistance. The reasons therefor are not sufficiently confirmed; however, it is considered that there is a probability of suppressing the generation speed of the chromium nitrides at a temperature of 700°C or less. It is desirable that 0.01% or more of Nb be contained in order to improve the corrosion resistance. On the other hand, in the case where an excessive amount of Nb is added, Nb is precipitated as non-solid-solubilized precipitates during heating before the hot rolling; and thereby, the toughness is inhibited. For this reason, the upper limit of the amount of Nb is set to 0.15%. In a case where Nb is added, the range of the amount is preferably in a range of 0.03% to 0.10%.
  • Ti is an element which forms oxides, nitrides, and sulfides in very small amounts and Ti refines crystal grains in the solidified structure and the structure heated at a high temperature of the steel.
  • Ti also has the property of replacing a part of the chromium in the chromium nitrides. With an amount of Ti of 0.003% or more, Ti precipitates are formed.
  • the upper limit of the amount of Ti is set to 0.05%.
  • a suitable amount of Ti is in a range of 0.005% to 0.020%.
  • B 0.0050% or less
  • Mg 0.0030% or less
  • REM 0.10% or less
  • B, Mg, and REM to be contained according to necessity are limited as follows.
  • B, Mg, and REM are all elements which improve the hot workability of the steel, and it is desirable that one or more be added for this purpose.
  • the addition of an excessive amount of any of B, Mg, and REM has the opposite effect of decreasing the hot workability and the toughness.
  • the upper limits of the above amounts are set as follows.
  • the upper limit of the amount of B is 0.0050%.
  • the upper limit of the amount of Mg is 0.0030%.
  • the upper limit of the amount of REM is 0.10%.
  • Preferable amounts of respective elements are B: 0.0005% to 0.0030%, Mg: 0.0001% to 0.0015%, and REM 0.005% to 0.05%.
  • REM is the sum of the amounts of lanthanoid rare earth elements such as Ce, La, and the like.
  • duplex stainless steel of the present embodiment by having the characteristics of the duplex stainless steel of the present embodiment described above, it is possible to greatly improve the hot manufacturability of the general-purpose duplex stainless steel which contains Sn.
  • a fracture reduction of area at 1000°C is in a range of 70% or more.
  • the processes which include the hot working it is possible to obtain a duplex stainless steel material with a high yield and few surface defects.
  • a cast steel with a thickness of 100 mm was prepared, and the fracture reduction of area was evaluated.
  • the evaluation was performed as follows. First, a parallel section of a round bar of 8 mm ⁇ was heated to 1200°C using a high frequency. Next, the temperature was lowered to a temperature (1000°C) at which a break test was performed. Tensile rupture was performed at a speed of 20 mm/second at this temperature, and the shrinkage of the cross section was measured.
  • the corrosion resistance of the steel plate was evaluated by the corrosion rate in sulfuric acid.
  • the corrosion rate in the sulfuric acid was measured as follows. Test pieces of 3 mm thick ⁇ 25 mm wide ⁇ 25 mm long were subjected to an immersion test for 6 hours in boiling 5% sulfuric acid. The weight before and after immersion was measured, and the rate of decrease in weight was calculated. Steels where the corrosion rate in the sulfuric acid was in a range of less than 0.3 g/m 2 per hour were evaluated as A (good), steels where the corrosion rate in the sulfuric acid was in a range of 0.3 to 1 g/m 2 per hour were evaluated as B (fair), steels where the corrosion rate in the sulfuric acid was in a range of 1 g/m 2 per hour or more were evaluated as C (bad), and the evaluation results are given in Tables 5 and 6.
  • the impact characteristics were measured using Charpy test pieces which were taken a long in the width direction.
  • the test pieces were prepared by processing 2 mm V notches at full size in the rolling direction. Testing was carried out at -20°C using two test pieces for each of the steels, and the impact characteristics were evaluated by the average values of the obtained impact values.
  • Steels where the impact value was in a range of more than 100 J/cm 2 were evaluated as A (good), steels where the impact value was in a range of 50 to 100 J/cm 2 were evaluated as B (fair), steels where the impact value was less than 50 J/cm 2 were evaluated as C (bad), and the evaluation results are given in Tables 5 and 6.
  • the steel plates were subjected to a solutionizing heat treatment in the following manner.
  • the steel plate was inserted into a heat treatment furnace at 1050°C and heated for approximately 5 minutes. Next, the steel plate was taken out, and then was subjected to water cooling to room temperature.
  • the corrosion resistance of the steel plate was evaluated by the corrosion rate in the sulfuric acid.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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  • Heat Treatment Of Steel (AREA)
EP12842430.6A 2011-10-21 2012-10-17 Rostfreier duplexstahl, platte aus dem rostfreien duplexstahl und material aus dem rostfreien duplexstahl Active EP2770076B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2011231352A JP5329632B2 (ja) 2011-10-21 2011-10-21 二相ステンレス鋼、二相ステンレス鋼鋳片、および、二相ステンレス鋼鋼材
JP2011266351A JP5329634B2 (ja) 2011-12-06 2011-12-06 二相ステンレス鋼、二相ステンレス鋼鋳片、および、二相ステンレス鋼鋼材
PCT/JP2012/076821 WO2013058274A1 (ja) 2011-10-21 2012-10-17 二相ステンレス鋼、二相ステンレス鋼鋳片、および、二相ステンレス鋼鋼材

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EP2770076A1 true EP2770076A1 (de) 2014-08-27
EP2770076A4 EP2770076A4 (de) 2016-03-09
EP2770076B1 EP2770076B1 (de) 2019-12-04

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US (2) US20140255244A1 (de)
EP (1) EP2770076B1 (de)
KR (2) KR101632516B1 (de)
CN (1) CN103857816B (de)
ES (1) ES2768088T3 (de)
TW (1) TWI460293B (de)
WO (1) WO2013058274A1 (de)
ZA (1) ZA201402169B (de)

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WO2016120525A1 (en) * 2015-01-27 2016-08-04 Outokumpu Oyj Method for manufacturing a plate material for electrochemical process
EP3276028A4 (de) * 2015-03-26 2018-08-08 Nippon Steel & Sumikin Stainless Steel Corporation Ferrit-austenit-edelstahlblech mit hervorragender gescherter stirnseitenkorrosionsbeständigkeit

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TWI460293B (zh) 2014-11-11
KR101632516B1 (ko) 2016-06-21
TW201333223A (zh) 2013-08-16
KR20160028514A (ko) 2016-03-11
CN103857816B (zh) 2017-02-15
EP2770076A4 (de) 2016-03-09
ZA201402169B (en) 2015-04-29
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ES2768088T3 (es) 2020-06-19
KR101648694B1 (ko) 2016-08-16
EP2770076B1 (de) 2019-12-04

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