JP3149476B2 - Ingot making method of rare earth element containing low nitrogen steel - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a rare earth element containing
Suitable for ingot method of tool steel with low nitrogen content, especially for high V high speed tool steel which is used for cutting tools for cutting hard materials such as taps and end mills and has good formability by grinding the cutting tool itself. It relates to a simple ingot making method.

[0002]

2. Description of the Related Art In recent years, with the advancement of the performance of various machines, the hardness of members used has been increased. High-performance tool steel, which is a tool for cutting such members, is also required to have high performance. On the other hand, in order to improve the strength and wear resistance of high-speed tool steel, the V content is increased. However, in this case, the grindability of the cutting tool itself tends to be reduced due to the coarsening of the VC carbide. Therefore, in order to refine the VC carbide and obtain good grindability, N, Ti, Nb, T
a) Regulation of content (JP-A-62-111354), addition of rare earth elements (hereinafter abbreviated as REM) and addition of Zr and Hf (JP-A-62-1621).
-21354, JP-A-57-3742, JP-A-6
1-213350), Al alone or co-addition with REM (JP-A-63-213641), Ca alone or co-addition with Al, REM (JP-A-1-252),
Regulations on Ti and N content to effectively utilize the effect of adding REM (Japanese Patent Laid-Open No. 62-21354, Japanese Patent Laid-Open No. 1-14)
Many proposals on chemical components have been made, such as regulation of the content of Ti and N in order to effectively utilize the effect of adding Al alone or jointly with REM (Japanese Patent Application Laid-Open No. 1-142056). In summary, in order to improve the grindability by refining the VC carbide of high-speed tool steel, which imparts strength and wear resistance by adding V, to improve the grindability, and to facilitate forming into tools, N, Ti, Regulating Nb, Ta, etc., REM, A
It is effective to add l, Ca, Zr, Hf and the like. However, according to the experience of the present inventors, N is particularly effective as the element to be regulated, and REM, Al is particularly effective as the element to be added. Can be achieved.

On the other hand, as equipment for melting high-speed tool steel,
Generally, an arc furnace and a high-frequency induction furnace are used, but since these are both dissolved in the atmosphere, N
Pickup is inevitable. In particular, in the case of a high-speed tool steel with an increased V content, the pick-up amount of N is large because the affinity between V and N is large. Furthermore, the adverse effects of dissolution in the atmosphere also extend to the control of REM and Al content. In particular, because REM has a high affinity for oxygen, in dissolution and casting in the atmosphere, unless other measures are taken. The addition yield of REM is extremely low, and if it is remarkable, the residual amount of REM in the steel ingot becomes about a mark. Therefore, many proposals have been made for a method for reducing N and a method for adding REM. Speaking of the method of melting tool steel having an increased V content, for example, use of a vacuum induction / degassing melting furnace is disclosed in Japanese Patent Application Laid-Open Nos.
No. -21354.

However, according to the findings of the present inventors, since the vacuum induction furnace has a large degassing effect, N can be easily reduced to 100 ppm or less by using this furnace, but REM was added. In this case, there are problems in the following points.
That is, since REM is extremely reactive, even in a vacuum induction furnace, not only does it react with a small amount of oxygen in the melting atmosphere, but also the refractory of the lining of the melting furnace and the equipment used for the casting system ( Usually, the active element oxide) is reduced and becomes itself an oxide to be mixed into the molten metal. Moreover, the mixed R
The oxide of EM has a large specific gravity (6 or more), and the floating separation from the molten metal is extremely slow. Therefore, from the REM addition to the completion of casting into a mold, REM oxides proceed to agglomerate, but since they are suspended in the molten metal, REM produced by vacuum induction melting is added. The V-based high-speed tool steel is clean as compared with the air-melted product, but is significantly inferior in cleanliness as compared with the case where no REM is added. In particular, when there are large inclusions in which the REM oxides are agglomerated on the outer periphery of the steel ingot, cutting tools such as taps and end mills, which are the main applications of the high-V high-speed tool steel, are used to cover the outer periphery. Since it is used, it shortens the tool life and further becomes the starting point of surface flaws during hot working of steel ingots,
Manufacturing yields also suffer significantly. Therefore, when manufacturing REM-added high-V high-speed tool steel or the like, improvement of cleanliness is an essential issue.

[0005]

SUMMARY OF THE INVENTION The present invention relates to the above-mentioned high V
It is an object of the present invention to provide a method for ingot of a rare earth element-containing low nitrogen steel having high grindability and high cleanliness, such as high-speed tool steel. It should be noted that the high V which is the main target of the present invention
The system high-speed tool steel has, for example, the following chemical components. That is, in terms of weight ratio, C: 0.9 to 1.5%, Si: 2% or less, Cr: 3 to 6%, one or two of Mo and W are 2Mo + W.
14-25%, V 2-5%, N: 100 ppm or less, rare earth element: 0.005
0.20.2%, Al 0.002〜0.3%, or Co: 15% or less, with the balance being Fe and unavoidable impurities.

[0006]

According to the present invention, there is provided a first step in which a consumable electrode having a nitrogen content of less than 100 ppm is melted by a vacuum induction furnace, and the consumable electrode contains a rare earth element compound. A method of ingot-making a rare earth element-containing low nitrogen steel, comprising a second step of remelting electroslag using a flux. Here, it is desirable that the rare earth element compound contained in the electroslag re-melting flux is at least one of an oxide and a fluoride.

[0007]

According to the present invention, the effect of degassing nitrogen and oxygen by a vacuum induction furnace and the electroslag remelting method (hereinafter referred to as E
By combining the cleaning in the SR method) and the REM addition effect by using a REM compound as the flux used for the REM compound, or the effect of improving the addition yield, N is easily reduced to 100 ppm or less, and 0.005 to 0.2% of REM is contained. In addition, it is possible to ingot REM-containing low-nitrogen steel such as high-V high-speed tool steel that is clean and excellent in hot workability. It has already been mentioned that a vacuum induction furnace can easily obtain low nitrogen steel. According to the present invention, the REM can be added from the flux in the ESR without performing the melting in a vacuum induction furnace. However, in order to obtain an accurate amount of the REM, the REM must be added during the production of the electrode. It is better to keep it.

An ESR method is known as one of the methods for improving the cleanness of a steel ingot. In the ESR method, a lower part of a consumable electrode produced by melting in another furnace is immersed in a molten slag in a water-cooled metal crucible, and a DC or AC current is supplied to a circuit composed of a consumable electrode, a molten slag and a steel ingot. By supplying electricity, the consumable electrode is melted from the lower side by the Joule heat of the molten slag to be melted and dropped into the slag in the crucible to produce a steel ingot. One feature of the ESR ingot is that a uniform and dense solidified structure is obtained by lamination solidification. Another feature is the refining effect of the molten slag. The molten droplet formed by dissolving the lower part of the consumable electrode leaves the tip of the consumable electrode, settles in the molten slag, and drops onto the molten metal part (pool) at the head of the growing steel ingot.
During this time, the molten metal is protected from the atmosphere by the molten slag, is subjected to refining effects such as deoxidation and desulfurization by contact with the molten slag, and inclusions are also absorbed by the slag. In the ESR melting, it is considered that the surface tension promotes the discharge of inclusions to the surface of the molten metal at the stage of forming the molten metal film at the tip of the consumable electrode, and the inclusions can be removed very easily. Further, even if the inclusions are settled in the molten slag while being contained in the inside of the molten droplet and reach the molten pool, separation by floating is easy because the molten material does not reach the lower portion of the molten pool. Therefore, by adopting the ESR method, it is expected to improve the cleanliness of the REM-added high-V high-speed tool steel and the like.

However, when the ESR method is applied to the high V
A major problem in application to high-speed tool steels is that if slag mixed with CaF ₂ , Al ₂ O ₃ , CaO, etc., used in normal ESR, is used, REM is uniformly applied to the ESR steel ingot.
Is not easy to add. This is because, for example, even if REM is contained in the consumable electrode, when the above-mentioned ordinary slag is used, the oxygen potential in the molten slag is high, and the addition yield of REM is significantly reduced due to oxidative consumption of REM. It is. On the other hand, a method of adding REM compounds (oxides, fluorides, etc.) to the slag, performing ESR dissolution by direct current, and adding REM to the molten metal by electrolytic reduction of the above compounds (Japanese Patent Publication No. Sho 46) (JP-A-36082) and a method of adding one or more REMs to a slag or a consumable electrode to perform ESR (JP-A-59-23811). In any of these, the REM compound in the slag and the consumable electrode are effectively alloyed into the steel ingot by blending the REM compound in the slag and reducing the oxygen potential in the slag by electrolytic reduction or further. In the former known example, DC melting is recommended, but as seen in the examples in the specification, REM is added to the steel ingot to such an extent that the effect of REM addition can be obtained even with AC melting. If it is desired to further increase the REM in the steel ingot, the REM may be added in advance to the consumable electrode as in the latter known example,
This is an effective method regardless of whether it is direct current or alternating current.

However, the main point of the above proposal is to effectively add REM to the steel ingot in the ESR method, and as described above, REM-added high-V high-speed tool steels and the like exhibit high performance. The other condition, the regulation of N, cannot be solved at all. This is ESR
Since the method dissolves in the atmosphere, if no measures are taken, the N in the steel ingot does not decrease as it increases, as suggested in JP-A-59-23811. Even if the slag surface is sealed with an inert gas such as argon in order to improve the REM addition efficiency, it is apparent from the fact that it has only an effect of suppressing the increase of N at most. Moreover, when the consumable electrode is melted in an arc furnace or a high-frequency induction furnace that is usually used for melting high-speed tool steel, an N content of 200 ppm or less is obtained no matter how carefully selected raw materials are used as described above. That is an extremely difficult task.

As can be seen from the above description, the present invention provides a degassing effect by a vacuum induction furnace, a cleaning by an ESR method, and a REM adding action by using a flux used for the purpose of containing a REM compound. Alternatively, it also has the effect of improving the yield of addition, thereby easily adding N 1
RE is 0.00ppm or less, contains 0.005 to 0.2% REM, improves machinability, is clean, and has excellent tool life and hot workability.
It becomes possible to ingot M-containing low N steel. When the means of the ingot making method of the present invention is used, an operation and effect that cannot be obtained by a combination of operations of applying a vacuum induction furnace and applying an ESR method, which are conventionally known, can be obtained. This is because, firstly, a new steel ingot method containing REM and having a low N of 100 ppm or less of nitrogen has not been known so far, and in order to meet this need, the conventional technology is described in the above. Like
At best, it was a countermeasure on chemical composition or a device in a single agglomeration method. Secondly, in order to achieve the new steel ingot casting method targeted by the present invention, vacuum induction melting is used to reduce the NEM, which cannot be achieved by the ESR method, together with REM.
Can be added to compensate for the risk of N increase in the ESR method and the yield instability of REM. On the other hand, ES
R method in steel cannot be achieved only by vacuum induction melting
In order to obtain a uniform distribution of
A special means of re-dissolving using a flux containing a REM compound which is not usually used is employed. As described above, the means of the ingot making method of the present invention is such that each element is complementary to each other, and for the first time, N is 100 ppm or less and REM content is 0.005 to 0.2%, thereby improving machinability and improving cleanability. It is possible to ingot REM-containing low N steel which is also excellent in hot workability, and the tool manufactured by applying existing processes such as rolling to the tool has a dramatically improved life. is there.

Next, the recommended alloy composition range of the REM-containing low-N steel suitable for the ingot-making method of the present invention will be described. C is Cr,
It combines with carbide-forming elements such as W, Mo, and V to form carbides, imparts quenching-tempering hardness, and contributes to wear resistance, heat resistance, and seizure resistance. If the content is too large, the toughness is reduced and a large carbide is generated. Therefore, it is desirable to contain the Cr, W, Mo, and V in a balanced amount, and to limit the content to 0.9 to 1.5%. Si is preferably added at 2% or less mainly for the purpose of deoxidation. Cr improves the high-temperature strength and the tempering softening resistance by setting the hardenability, the wear resistance, the oxidation resistance, and the appropriate content. Although it is set to 3% or more for the above purpose, if it is too large, the high-temperature strength and the tempering softening resistance are reduced, and the toughness is also reduced. W and Mo combine with C to form a special carbide and contribute to improvement of wear resistance and seizure resistance. In addition, the secondary hardening effect by tempering is large, and contributes to high-temperature strength. In order to obtain the above-mentioned effects, it is added so that the amount of 2Mo + W satisfies 14 to 25%. If the amount of 2Mo + W is less than 14%, the above effects cannot be sufficiently obtained. If the amount is too large, toughness and hot workability are impaired.
+ W 25% or less is desirable.

V combines with C to form a hard carbide,
Contributes to improved wear resistance. However, since the carbide is harder than the abrasive grains, it causes the grinding wheel to be worn out early. In particular,
If a large number of coarse carbides are generated and the distribution is not uniform, the grindability will be significantly reduced. For this reason, conventionally, when the grindability was emphasized, it was limited to about 1.2% or less. However, according to the present invention, the addition of REM and the reduction of N can prevent the generation of MC type carbide mainly composed of coarse V even if a large amount of V is contained. An appropriate amount is contained in the range of ~ 5%. If it exceeds 5%, the effect of the present invention is reduced, so that the content is set to 5% or less, and if it is too small, it does not sufficiently contribute to wear resistance, so it is good to set it to 2.0% or more. N is an impurity which becomes an eye of the method of the present invention. N amount
If it exceeds 100 ppm, it is set to 100 ppm or less to impair the VC miniaturization effect due to the addition of REM. REM has the effect of increasing the absolute amount of MC type carbide and the effect of crystallizing VC carbide finely. If it is less than 0.005%, these effects are small, and if it exceeds 0.2%, it combines with S and O to form inclusions and causes casting defects. Therefore, the content is preferably limited to 0.005 to 0.2%. Al has the effect of reducing the activity of oxygen in molten steel, suppresses the formation of oxides of REM, and promotes the VC refining effect of REM. If it is less than 0.002%, this effect is small, and if it exceeds 0.3%, Al oxides increase to deteriorate the cleanliness. Co forms a solid solution in the matrix to improve the above strength and heat resistance and does not directly contribute to the control of the carbide morphology and the improvement of the cast structure according to the present invention, but is added at 15% or less as necessary.

[0014]

EXAMPLE The raw materials were charged into a 6-ton nominal vacuum induction furnace and melted in a vacuum (however, Table 1, No. 4 is an atmospheric induction furnace). In a vacuum induction furnace, the pressure in the tank is
The solubility was maintained at 100 ppm or less. After all the component adjustments other than the REM were completed and it was confirmed that the N content of the molten metal was 100 ppm or less, the required amount of the REM was added into the furnace, and the steel was tapped into a ladle. Further, a consumable electrode was produced by casting in a mold having a predetermined shape in a vacuum (excluding No. 4) (however, No. 5).
Is cast into ingot). The chemical components of the consumable electrodes thus produced are shown in Table 1, No. 1, 2, 3, 4, 6, 7 in the upper "electrode". Here, the vacuum induction furnace is represented by VIF. VIF
REM in the consumable electrode is 0.04 to 0.06% as shown in the REM (electrode) column of the table, and the addition yield of REM is 59 to 73% as shown in the REM yield (electrode) column. N is 2
It was in the range of 9-39 ppm. Use the above consumable electrode with AC ESR
Was carried out to obtain a steel ingot. The amount of flux used in ESR is about 50 kg per ton of consumable electrode charged. Also, ES
In order to prevent [N] contamination from the atmosphere during R
Dissolution was performed by replacing with r gas. Nos. 1 and 2 have almost the same chemical components as the electrodes.
No. 7 is an example in which Co is increased with respect to Nos. 1, 2, and No. 7 is an example in which Co is excluded from Nos. 1, 2 with an increase in the amount of W and V and a decrease in Mo. In these embodiments of the present invention, the ESR
The REM in the steel ingot is 0.03-0.05%, and the REM in the consumable electrode is
The yield to EM was 67 to 83%, and N in the ESR ingot was in a sufficiently low range of 42 to 53 ppm.

On the other hand, Nos. 3 to 5 in Table 1 are comparative examples.
No.3 is the same basic chemical composition as No.1 and No.2, when the consumable electrode is melted in a vacuum induction furnace and ESR is performed without blending the REM compound into the flux. Melting consumable electrodes in a furnace and applying REM to ESR flux
In the case where the compound was blended, No. 5 is a case where the steel ingot was directly formed in a vacuum induction furnace without performing ESR. Comparing the chemical components, in No. 3, the RE of the consumable electrode was lower than that of the present invention.
Although M is almost the same as 0.06%, after ESR
As low as 0.01%, the REM yield in the ESR was about 17%, compared to 67-83% for the present invention example as described above. In No. 4, the REM was 0.02%, which is relatively close to the value of the present invention, but the N value was close to 200 ppm for both the consumable electrode and the ESR ingot. No. 5 is equivalent in chemical composition to the present invention.

[0016] The above seven steel ingots were subjected to hot ingot forging to obtain 10 ingots.
It was formed into a billet of 0 mm square. At this time, the steel ingot weight W _I k
g, riser like ingot wastepaper weight W _R kg, when the billet weight after the removal of surface defects by a grinder and W _B kg,
The hot working yield A (%) is represented by the following equation. _{A = {W B / (W} I -W R)} × 100 is shown in conjunction with this hot working yield in Table 2 below, ESR
The ingots (except No. 5) all accounted for 90% or slightly below this, whereas those obtained directly in a vacuum induction furnace (VIF) (No. 5) accounted for 71%. In addition, when the scratched portion of No. 5 was examined in detail, a large amount of nonmetallic inclusions mainly composed of oxides, oxysulfides, etc. of REM were found.

After annealing each billet, hot wire rolling was performed, followed by annealing to obtain a wire. Furthermore, these materials were cold-drawn and ground to form steel bars with a diameter of 6.23 mm, and various material properties were evaluated. As the evaluation items, the interposition article position, the amount of VC carbide, the heat treatment hardness, the micro bending strength, and the grindability with respect to the moldability of the tool itself were evaluated.
In addition, a tap was actually manufactured into an equal diameter hand tap for Japanese Industrial Standard Coarse Thread, and the cutting life was evaluated. The heat treatment was performed at 560 ° C. for 1 hour after quenching a salt bath at 1220 ° C. for three times. The results of these evaluations are shown in Table 2 together with the hot working yield described above. The interposed article position of each sample was determined as follows: B + C, based on Japanese Industrial Standards, for the center of a flat surface of a bar that had been subjected to the above heat treatment and polished with a diamond grindstone from the surface layer parallel to the axis to a depth of about 1/8 of the material diameter. Of inclusions were measured. FIG. 1 shows an example of inclusion microscopy of samples Nos. 1 and 3 to 5 among them. Further, the central portion of the plane created in the same manner was polished with chromium oxide, and VC carbide was observed. An example of this organization is shown in FIG.

[0018]

[Table 1]

[0019]

[Table 2]

The VC area ratio of each sample was determined in the same manner as in the above-described inclusion measurement, by polishing a diamond whetstone, corroding with 10% nitric alcohol and further corroding with Murakami reagent, and measuring the total visual field area of 94,000. The VC carbide in μm ² was measured. The heat treatment hardness of each sample was measured with a Vickers hardness meter at a load of 30 kg on a plane obtained in the same manner as the above-described inclusion measurement. In addition, the micro-section bending strength is obtained by grinding and cutting a 0.8 mm thick thin plate, including the central axis of the steel bar, and measuring about 1/8 of the material diameter from the surface layer of the material in the thin plate. The load was applied so that the portion became a fracture surface. The machinability was evaluated by taking a thin plate of 2 mm thickness, including the axis, from the heat-treated steel bar. From the surface layer of the material, a portion near one-eighth of the material diameter was measured.
Wet plunge grinding was performed with a surface grinder using a grinding wheel A, and the ratio was determined as the ratio between the amount of grinding wheel wear after the grinding test and the amount of grinding removal of the sample. Table 3 shows the grinding conditions.

[0021] ↓

[Table 3] ↑

The results of the inclusion tests of the inventive examples of Nos. 1, 2, 6, and 7 are all sufficiently lower than that of No. 5 by VIF. Further, as shown in FIG. 2, the VC carbides having a size of 5 μm or more (2 mm in the photograph of × 400) were very small and finely distributed. Although not shown, No. 7 had the largest number of VC carbides and was finely distributed in the examples of the present invention. On the other hand, in the case of No. 3, almost no REM remains at 0.01%, so that the VC carbide is not sufficiently refined. No. 4 is N
Since the amount is high, VC carbides are coarsely crystallized. No.
In No. 5, a fine structure was obtained for VC carbide. However, as described above, a large number of REM oxysulfides and the like were found in which the position of the intervening article was poor and somewhat large. As for the heat treatment hardness, a hardness of HV880 or more was obtained in all cases, and a high hardness of about HV910 was obtained in No. 6 to which a little Co was added.
In the micro bending strength, the VC carbides and inclusions of Nos. 1, 2, 6, and 7 of the present invention in which a fine structure was obtained were all 250 kgf except that the high VC area ratio No. 7 was slightly lower. High strength of about / mm ² or more was obtained. In Nos. 3 to 5, the strength was slightly lower than that of the examples of the present invention, probably because the VC carbides or inclusions were slightly coarse. Regarding the grindability, No. 3, 4 with a large amount of VC carbide of 5 μm or more has a large grinding wheel wear amount and a small grinding ratio, while the other samples have a grinding ratio of about 10, which is obtained. The value indicates that the grindability is almost the same as SKH55. The tap cutting test for each sample was performed using a 12mm thick S
A cutting test was performed using a 45C plate by drilling a pilot hole with an inner diameter of 5.0 mm. Table 4 shows the tap cutting test conditions. The cutting life was evaluated by the number of cut holes until the tap was broken or the internal thread precision exceeded the tolerance set by Japanese Industrial Standards.

[0023] ↓

[Table 4] ↑

[0024] To overcome the general commercial tap tool life is 4% or more VC weight area ratio, HV880 or more hardness is obtained, for耐刃chipping improvement, 220 kgf / mm ² or more micro It is necessary to have a transverse rupture strength. All of the examples of the present invention sufficiently satisfied this condition, and a longer life was obtained as compared with Nos. 3 to 5 of the comparative examples.

[0025]

As described above, according to the present invention, it is possible to produce a steel containing REM and having a low N with a high degree of cleanliness, which has been difficult with the conventional ingot making method. As a result, the grindability and tool life were greatly improved. Also,
Compared with the vacuum induction melting method, the hot working yield is greatly improved,
The reduction in production cost more than compensates for the cost increase due to double melting.

[Brief description of the drawings]

FIG. 1 is a metallographic micrograph showing the microstructure of inclusions of a representative sample.

FIG. 2 is a metallographic micrograph showing a VC carbide of a representative sample.

──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. ⁷ Identification code FI C22B 9/18 C22C 38/00 302E 9/187 38/22 C22C 38/00 302 38/30 38/22 38/34 38/30 C22B 9/18 A 38/34 F (72) Inventor Norimasa Uchida 2107-2, Yasugi-cho, Yasugi-shi, Shimane Hitachi Metals, Ltd. Yasugi Plant (72) Inventor Hideki Nakamura 2107-2, Yasugi-cho, Yasugi-shi, Shimane Inspector, Hitachi Metals, Ltd. Yasugi Plant Shunji Fukasaka (56) References JP-A-62-44535 (JP, A) JP-A-3-146624 (JP, A) JP-A-61-213350 (JP, A) Iron And steel, 72 [4] (1986) p. 226 (58) Field surveyed (Int.Cl. ⁷ , DB name) C21C 5 / 52,7 / 00 B22D 23/10 C22B 9 / 18,9 / 187 C22C 38 / 00,38 / 22 C22C 38/30, 38/34 JICST File (JOIS)

Claims (3)

(57) [Claims] 1. The nitrogen content is 100 ppm by a vacuum induction furnace.
A rare earth element-containing consumable electrode, and a second step of electrodissolving the consumable electrode using a flux containing a compound of a rare earth element. Ingot making method for low nitrogen steel. 2. The rare-earth element-containing low-nitrogen steel according to claim 1, wherein the rare-earth element compound contained in the electroslag remelting flux is at least one of an oxide and a fluoride of the rare-earth element. Ingot making method. 3. The rare-earth-element-containing low-nitrogen steel in weight ratio,
C: 0.9 to 1.5%, Si: 2% or less, Cr: 3 to 6%, one or two of Mo and W at 2 Mo + W 14 to 25%, V 2 to 5%, N: 100 ppm
Hereinafter, rare earth elements: 0.005 to 0.2%, Al 0.002 to 0.3%, or Co: 15% or less, and the balance is Fe and inevitable impurities. The ingot making method for rare earth element-containing low nitrogen steel according to claim 1 or 2.